Patent Application
20100326572
This disclosure relates to a method for producing a high-strength cold-rolled steel sheet for press forming which is used for automobiles, home electric appliances, and the like through a press forming process.
BFI steel sheets with 340 MPa grade in tensile strength (bake-hardenable steel sheets, simply referred to as “340BH” hereinafter) and IF steel sheets with 270 MPa grade in tensile strength (Interstitial Free steel sheets, simply referred to as “270IF” hereinafter), which is ultra-low-carbon steel containing carbide/nitride-forming elements such as Nb and Ti to control the amount of dissolved C, have been applied to automotive outer panels, such as hoods, doors, trunk lids, back doors, and fenders, which are required sufficient dent resistance.
In recent years, regarding the increasing requirement of further weight reduction of car bodies, new attempt of applying steel sheet with higher strength and superior dent resistance has been carried out to reduce thickness of the steel sheet for outer panel. Also investigations to improve dent resistance and to decrease the temperature and time of a baking finish process while maintaining the current thickness have progressed in view of applying higher strength steel sheet.
However, when a solution-hardening element such as Mn, P, or the like is further added to 340BH with a yield strength YP of 230 MPa or 270IF with a YP of 180 MPa to strengthen and thin a steel sheet, surface distortion occurs. The term “surface distortion” represents micro wrinkles or wavy patterns produced in a press-formed surface due to an increase in YP. The occurrence of surface distortion impairs the design or design property of a door, a trunk lid, or the like. Therefore, the steel sheet for that application is desired that YP after press forming and baking finish treatment is increased more than YP of a conventional steel sheet while maintaining extremely low YP before press forming.
In such a background; for example, Japanese Examined Patent Application Publication No. 62-40405 discloses a method for producing a steel sheet having low YP, high work-hardenability WH, and high BH by appropriately controlling the cooling rate after annealing steel to form a dual phase mainly composed of ferrite and martensite, the steel containing 0.005 to 0.15% of C, 0.3 to 2.0% of Mn, and 0.023 to 0.8% of Cr. In addition, Japanese Unexamined Patent Application Publication No. 2006-233294 discloses a method for producing a high-strength cold-rolled steel sheet having high BH by annealing steel which contains 0.01% to 0.04% of C, 0.3 to 1.6% of Mn, 0.5% or less of Cr, and 0.5% or less of Mo and which satisfies 1.3≦Mn+1.29Cr+3.29Mo≦2.1% and cooling at a cooling rate of 100° C./sec or more in the temperature range of at least 550° C. or lower to increase the amount of dissolved C in the steel. Japanese Unexamined Patent Application Publication No. 2006-52465 discloses a method for producing a high-strength cold-rolled steel sheet including ferrite and a low-temperature transformed phase and having high BH and excellent surface appearance quality after press forming, the method including annealing steel which contains 0.0025% to less than 0.04% of C, 0.5 to 2.5% of Mn, and 0.05% to 2.0% of Cr, cooling at a cooling rate of 15 to 200° C./sec in the temperature range of 650° C. to 450° C., and further cooling at a cooling rate of less than 10° C./sec in the temperature range of 200° C. to near 300° C.
However, the high-strength cold-rolled steel sheets produced by the methods described in Japanese Examined Patent Application Publication No. 62-40405 and Japanese Unexamined. Patent Application Publication Nos. 2006-233294 and 2006-52465 have the following problems:
It could therefore be helpful to provide a method for producing a high-strength cold-rolled steel sheet with low YP and excellent uniformity.
We conducted investigations on methods for further decreasing YP while maintaining high BH equivalent to or higher than a general value and decreasing variation in mechanical properties with respect to a dual phase high-strength cold-rolled steel sheet. As a result, the following findings were obtained:
We thus provide a method for producing a high-strength cold-rolled steel sheet, the method including hot-rolling and cold-rolling steel having a composition which contains, by % by mass, over 0.01% to less than 0.08% of C, 0.2% or less of Si, 0.8% to less than 1.7% of Mn, 0.03% or less of P, 0.02% or less of S, 0.3% or less of sol. Al, 0.01% or less of N, and over 0.4% to 2% of Cr, and which satisfies 1.9<[Mneq]<3 and 0.34≦[% Cr]/[% Mn], the balance being composed of iron and inevitable impurities; heating at an average heating rate of less than 3° C./sec in a temperature range of 680° C. to 740° C.; annealing at an annealing temperature of over 740° C. to less than 820° C.; cooling at an average cooling rate of 2 to 30° C./sec in the temperature range of the annealing temperature to 650° C.; cooling at an average cooling rate of 10° C./sec or more in the temperature range of 650° C. to Tc° C. represented by the equation (1) below; and cooling at an average cooling rate of 0.2 to 10° C./sec in the temperature range of Tc° C. to 200° C.
Tc=410−40×[% Mn]−30×[% Cr] (1)
Here, [Mneq] represents the Mn equivalent shown by [Mneq]=[% Mn]+1.3×[% Cr] and [% Mn] and [% Cr] represent the contents of Mn and Cr, respectively.
In the method for producing the high-strength cold-rolled steel sheet, heating is preferably performed at an average heating rate of less than 2° C./sec in the temperature range of 680° C. to 740° C. during annealing.
Further, preferably, steel satisfying 0.55≦[% Cr]/[% Mn] is used, and 0.005% by mass or less of B is contained. In addition, at least one of 0.15% by mass or less of Mo and 0.2% by mass or less of V is preferably contained. Further, at least one of less than 0.014% by mass of Ti, less than 0.01% by mass of Nb, 0.3% by mass or less of Ni, and 0.3% by mass or less of Cu is preferably contained.
A high-strength cold-rolled steel sheet with low YP and excellent uniformity can be produced. The high-strength cold-rolled steel sheet produced by the method has excellent resistance to surface distortion and excellent dent resistance and is thus suitable for strengthening and thinning automotive parts.
Our steels and methods will be described in detail below. “%” indicating the content of a component represents “% by mass” unless otherwise specified.
C is an element necessary for securing a predetermined amount of a second phase. When the C content is excessively low, the second phase cannot be secured in a sufficient amount, and low YP cannot be achieved. Further, sufficiently high BH cannot be secured, and the anti-aging property is degraded. The C content is required to exceed 0.01% to secure a sufficient amount of the second phase. On the other hand, when the C content is 0.08% or more, the ratio of the second phase is excessively increased with a result that YP increases. Therefore, the upper limit of the C content is less than 0.08%. The C content is preferably less than 0.06% for achieving lower YP and more preferably less than 0.04% for achieving further lower YP.
Si has the effect of delaying scale formation in hot rolling and improves surface appearance quality when added in a small amount, the effect of further homogenizing and coarsening the microstructure of a steel sheet, and the effect of improving seizing to a mold (mold galling) in press forming. Therefore, Si can be added from this viewpoint. However, Si has a large solution-hardening ability and thus has the large effect of increasing YP. Therefore, the Si content is in the range of 0.2% or less which causes little influence on an increase in YP. The C content is preferably 0.1% or less.
Mn: 0.8% to Less than 1.7%
Mn can enhance hardenability and decrease the amount of dissolved C in a predetermined range by appropriately controlling the Mn content to decrease YP and increase BH. When the Mn content is 0.8% or less, the amount of dissolved C is excessively increased in a cooling step of annealing, and a large amount of dissolved C precipitates in strain around martensite during overaging treatment in the temperature range of less than 400° C., causing difficulty in sufficiently decreasing YP. In addition, when the amount of dissolved C is excessively increased, anti-aging property is degraded. On the other hand, when the Mn content is 1.7% or more, the amount of dissolved C is excessively decreased, thereby decreasing BH. Further, solid-solution hardening of Mn is increased, and a second phase is made fine increasing YP and cause variation of YP with annealing temperature. Therefore, the Mn content is 0.8% to less than 1.7%.
P has a large solution hardening ability and is preferably added in as small an amount as possible from the viewpoint of decreasing YP. However, P has the effect of further coarsening the microstructure of a steel sheet and the effect of improving seizing to a mold (mold galling) in press forming. Therefore, the P content is 0.03% or less which has a small adverse effect on an increase in YP.
S precipitates as MnS in steel but decreases the ductility of a steel sheet and decreases press formability when added in a large amount. In addition, hot ductility is decreased in hot rolling of a slab, and thus surface defects easily occur. Therefore, the S content is 0.02% or less but is preferably as low as possible.
Sol. Al: 0.3% or Less
Al is used as a deoxidizing element or an element for improving the anti-aging property by fixing N as AlN. However, Al forms fine AlN during coiling or annealing after hot rolling to suppress the growth of ferrite grains and inhibit reduction in YP. From the viewpoint of decreasing oxides in steel or improving anti-aging property, Al is preferably added in an amount of 0.02% or more. On the other hand, from the viewpoint of improving the grain growth property, the ferrite grain growth property is improved by increasing the coiling temperature to 620° C. or more, but the amount of fine AlN is preferably as small as possible. Therefore, preferably, the sol. Al content is 0.15% or more, and AlN is coarsely precipitated during coiling. However, since the cost is increased when the sol. Al content exceeds 0.3%, the sol. Al content is 0.3% or less. In addition, when the sol. Al content exceeds 0.1%, castability is impaired to cause deterioration of the surface appearance quality. Therefore, the sol. Al content is preferably 0.1% or less for application to exterior panels which are required to be strictly controlled in surface appearance quality.
N precipitates during coiling or annealing after hot rolling to form fine AlN and inhibit the grain growth property. Therefore, the N content is 0.01% or less but is preferably as low as possible. In addition, an increase in the N content causes deterioration of the anti-aging property. From the viewpoint of improving the grain growth and anti-aging property, the N content is preferably less than 0.008% and more preferably less than 0.005%.
Cr is the most important element. Since Cr has a small amount of solid-solution hardening and the effect of making fine martensite as the second phase and enhancing hardenability, Cr is an element effective in decreasing YP and decreasing variation in material quality. It is necessary to control the Mn equivalent and the composition ratio to Mn to exhibit these effects, which will be described below, and the Cr content is necessary to exceed 0.4%. On the other hand, when the Cr content exceeds 2%, the cost is increased, and the surface appearance quality of a galvanized steel sheet is degraded. Therefore, the Cr content is 2% or less.
When the Mn equivalent, i.e., the [Mneq], is controlled to exceed 1.9 by controlling the cooling rate in annealing, the amount of dissolved C is decreased to a proper range, and the formation of pearlite and bainite is suppressed to decrease YP and increase BH. Further, from the viewpoint of decreasing YP, [Mneq] preferably exceeds 2.1 and more preferably exceeds 2.2. On the other hand, when [Mneq] is excessively increased, BH is decreased, and the cost is increased. Therefore, [Mneq] is less than 3.
When the ratio of the Cr content to the Mn content, i.e., [% Cr]/[% Mn], is controlled to 0.34 or more while [Mneq] is constant, the second phase can be coarsened and solid-solution hardening of Mn can be decreased, thereby decreasing YP and material quality variation. To further decrease YP and material quality variation, 0.55≦[% Cr]/[% Mn] is preferred.
The balance includes iron and inevitable impurities, but the elements below may be contained at predetermined contents.
Similarly, B is an element for enhancing hardenability and has the function to fix N as BN to improve the grain growth property. However, when B is excessively added, the second phase is inversely made fine by the influence of residual dissolved B. Therefore, the B content is preferably 0.005% or less. The effect of improving the ferrite grain growth property can be sufficiently exhibited by adding over 0.001% of B, thereby achieving extremely low YP. Therefore, the B content preferably exceeds 0.001%.
Like Mn and Cr, Mo is an element for enhancing hardenability and can be added for the purpose of improving hardenability. However, when Mo is excessively added, like Mn, the second phase is made fine and hard, increasing YP. Therefore, Mo is preferably added in the range of 0.1% or less which has the small influence on an increase in YP. From the viewpoint of further decreasing YP and ΔYP, the Mo content is preferably less than 0.02% (not added).
Similarly, V is an element for enhancing hardenability. However, when V is added in an amount exceeding 0.2%, the cost is significantly increased. Therefore, V is preferably added in the range of 0.2% or less.
Ti: Less than 0.014%
Ti has the effect of improving the anti-aging property by fixing. N and the effect of improving castability. However, Ti forms fine precipitates of TiN, TiC, Ti(C, N), and the like in steel to inhibit the grain growth property. Therefore, from the viewpoint of decreasing YP, the Ti content is preferably less than 0.014%.
Nb: Less than 0.01%
Nb has the effect of delaying recrystallization in hot rolling controlling the texture and decrease YP in a direction at 45 degrees with the rolling direction. However, Nb forms fine NbC and Nb(C, N) in steel to significantly degrade the grain growth property and increase YP. Therefore, Nb is preferably added in the range of less than 0.01% which has a small influence on an increase in YP.
Cu is an element mixed when scraps or the like are positively utilized and a recycled material can be used as a raw material when Cu is allowed to be mixed, thereby decreasing the production cost. Cu has a small influence on the material quality, but mixing of excessive Cu causes surface flaws. Therefore, the Cu content is preferably 0.3% or less.
Ni also has a small influence on the material quality of a steel sheet, but Ni can be added from the viewpoint of decreasing surface flaws when Cu is added. However, when Ni is excessively added, surface defects due to heterogeneity of scales are produced. Therefore, the Ni content is preferably 0.3% or less.
As described above, the production method includes hot-rolling and cold-rolling a steel slab having the above-described composition, heating at an average heating rate of less than 3° C./sec in the temperature range of 680° C. to 740° C., annealing at an annealing temperature of over 740° C. to less than 820° C., cooling at an average cooling rate of 2 to 30° C./sec in the temperature range of the annealing temperature to 650° C., cooling at an average cooling rate of 10° C./sec or more in the temperature range of 650° C. to Tc° C. represented by the equation (1) described above, and cooling at an average cooling rate of 0.2 to 10° C./sec in the temperature range of Tc° C. to 200° C.
The slab can be hot-rolled by a method of rolling the slab after heating, a method of directly rolling the slab without heating after continuous casting, or a method of rolling the slab by heating for a short time after continuous casting. The hot rolling may be performed according to a general method, for example, at a slab heating temperature of 1100° C. to 1300° C., a finish rolling temperature of Ar3 transformation point or more, an average cooling rate after finish rolling of 10 to 200° C./sec, and a coiling temperature of 400° C. to 720° C. Preferably, the slab heating temperature is 1200° C. or less, and the finish rolling temperature is 840° C. or less to obtain beautiful plating appearance quality for an outer panel. In addition, descaling is preferably sufficiently performed for removing primary and secondary scales formed on the surface of the steel sheet. From the viewpoint of decreasing YP, the coiling temperature is preferably as high as possible and 640° C. or more. In particular, when the coiling temperature is 680° C. or more, Mn and Cr can be sufficiently concentrated in the second phase in the state of the hot-rolled sheet, and stability of γ in the subsequent annealing step is improved, contributing to a decrease in YP. To decrease in-plane anisotropy of r value of the steel sheet and suppress YP in a direction at 45° with the rolling direction, the cooling rate after finish rolling is preferably as large as 40° C./sec or more.
The rolling rate of cold rolling may be 50% to 85%.
It is effective to control the heating rate in the temperature region of 680° C. to 740° C. to uniformly disperse the coarse second phase after annealing and decrease YP and variation in material quality. This is because in a component system with [Mneq] of over 1.9, the second phase after annealing is easily made fine. It is considered that, when the Mn content is high, the Ac1 transformation temperature is excessively decreased, and y grains are formed in unrecrystallized ferrite grain boundaries before the completion of recrystallization. Even when recrystallization is completed, γ grains are produced in fine ferrite grain boundaries immediately after recrystallization. Therefore, YP of a steel sheet is easily increased.
Steel containing 0.028% of C, 0.01% of Si, 1.6% of Mn, 0.01% of P, 0.01% of S, 0.04% of sol. Al, 0.8% of Cr, and 0.003% of N was molten in a laboratory to produce a slab of 27 mm in thickness. The slab was heated to 1250° C., hot-rolled to 2.3 mm at a finish rolling temperature of 830° C., and then coiled for 1 hour at 620° C. The resultant hot-rolled sheet was cold-rolled to 0.75 mm with a rolling reduction of 67%. The resultant cold-rolled sheet was annealed at 780° C. for 40 seconds at an average heating rate changed from 0.3 to 20° C./sec in the range of 680° C. to 740° C., cooled at an average cooling rate of 7° C./sec in the temperate range from the annealing temperature to 650° C., cooled at 25° C./sec in the temperature range from 650° C. to 300° C., cooled at 0.5° C./sec in the temperature range from 300° C. to 200° C., and then air-cooled to room temperature. A JIS No. 5 tensile test piece was collected from the resultant steel sheet and subjected to a tensile test (according to JISZ2241, the tensile direction perpendicular to the rolling direction) and SEM observation of the structure.
At the annealing temperature of 740° C. or less, the second phase cannot be stably secured because of the insufficient solid solution of carbides. At the annealing temperature of 820° C. or more, the γ ratio is excessively increased in annealing, and elements such as Mn, C, and the like are not sufficiently concentrated in γ grains, thereby failing to achieve sufficiently low YP. This is possibly because when elements are not sufficiently concentrated in γ grains, strain is not sufficiently applied to the periphery of martensite, and pearlite and bainite transformation easily occurs in the cooling step after annealing. The holding time during annealing is preferably 20 seconds or more in the temperature range of over 740° C. which corresponds to usual continuous annealing, and is more preferably 40 seconds or more.
To concentrate Mn and Cr in γ grains during cooling to enhance hardenability of the γ grains and decrease YP, the average cooling rate in the temperature range of the annealing temperature to 650° C. is necessary to be 2 to 30° C./sec.
When cooling is performed at an average cooling rate of 10° C./sec or more in the temperature range from 650° C. to Tc° C. near the Ms point in which pearlite and bainite are easily produced, the formation of pearlite and bainite is suppressed, thereby achieving sufficiently low YP.
When cooling is performed at an average cooling rate of 0.2 to 10° C./sec in the temperature range from Tc° C. to 200° C., dissolved C which excessively remains in ferrite is precipitated to decrease YP and increase ductility.
The high-strength cold-rolled steel sheet produced by the method has yield point elongation (YPEI) of less than 0.5% and sufficiently decreased YP in an annealed state and thus can be used directly as a steel sheet for press forming. However, from the viewpoint of controlling surface roughness and stabilizing press formability by flattening a shape of steel sheet, skin pass rolling may be performed. In this case, from the viewpoint of decreasing YP and increasing El and WH, the elongation is preferably 0.3% to 0.5%.
Steel of each of Steel Nos. A to BB shown in Table 1 was molten and continuously cast into a slab of 230 mm in thickness. The slab was reheated to 1180° C. to 1250° C. and hot-rolled at a finish rolling temperature of 830° C. (Steel Nos. A to D, I, R to V, and X to BB) or 880° C. (Steel Nos. E to H, J to Q, and W). Then, the steel sheet was cooled at an average cooling rate of 20° C./sec and coiled at a coiling temperature of 540° C. to 640° C. The resultant hot-rolled sheet was cold-rolled with a rolling reduction of 67% to 78% after pickling to form a cold-rolled sheet of 0.75 mm in thickness. The resultant cold-rolled sheet was annealed at the average heating rate in the temperature range of 680° C. to 740° C., the annealing temperature, the primary average cooling rate in the temperature range of the annealing temperature to 650° C., the secondary average cooling rate in the temperature range of 650° C. to Tc° C., and the tertiary average cooling rate in the temperature range of Tc° C. to 200° C., which are shown in Tables 2 and 3. A JIS No. 5 test piece was collected from the resultant annealed steel sheet, i.e., the steel sheet not having undergone skin pass rolling, in each of the rolling direction and the perpendicular direction and subjected to a tensile test (according to JISZ2241) to evaluate YP and TS. In addition, the annealing temperature for the steel sheet with each of the compositions was changed in the range of 760° C. to 810° C. to measure the maximum and minimum of YP and determine variation ΔYP of YP. Further, prestrain of 2% was applied to the same test piece to determine an increase in YP after heat treatment at 170° C. for 20 minutes, i.e., BH.
The results are shown in Tables 2 and 3.
Our steel sheets exhibit low YP, i.e., low YR, as compared to a material in the same TS level. Our steel sheets also have ΔYP and are thus excellent in YP stability. In particular, in the steel sheet in which [Mneq] and [% Cr]/[% Mn] are appropriately controlled to over 2.1 and 0.55 or more, respectively, and the heating rate of annealing is controlled to less than 3° C./sec, solution hardening by Mn and dissolved C is decreased, and the second phase is uniformly coarsened, thereby decreasing YP and ΔYP. For example, in the steel of Steel Nos. B, C, and D, [Mneq] is increased as compared with the steel of Steel No. A, but [% Cr]/[% Mn] is in the range of 0.34 to 0.41. Therefore, the amounts of pearlite and bainite produced are decreased with increase in [Mneq], and the amount of dissolved C is decreased. However, the second phase is made fine to exhibit YP in the range of 191 to 197 MPa and ΔYP in the range of 7 to 9 MPa with annealing temperature under the conditions with a heating rate of 1.5° C./sec and an annealing temperature of 780° C.
On the other hand, in the steel of Steel Nos. E, F, G, and H in each of which [Mneq] is increased to over 2.1 and [% Cr]/[% Mn] is controlled to 0.55 or more, YP and ΔYP with annealing temperature are in the range of 172 to 198 MPa and the range of 4 to 6 MPa, respectively, and very low under the same conditions as Steel Nos. A, B, C, and D. In addition, an increase in YP due to an increase in C is extremely small, and Steel No. K in which the C content is increased to 0.058% has TS of 490 MPa and YP of as low as 208 MPa. Further, Steel No. L in which the C content is increased to 0.072% has TS of 541 MPa and YP of as low as 230 MPa. Namely, even when the C content is changed, a steel sheet with small ΔYP and low YR can be stably obtained. Further, since the composition ranges of Mn and Cr are appropriately controlled, high BH is achieved in spite of low YP.
However, a steel sheet in which [Mneq] and the heating rate and cooling rate in annealing arc not appropriately controlled has high YR as compared to our steel sheets in the same strength level. For example, Steel Nos. S and V in which [% Cr]/[% Mn] is not appropriately controlled have the fine second phase and the large amount of solution hardening and thus have high ΔYP and YP and low BH. Steel No. T containing Mo has the tendency to form a fine microstructure, increasing YP and ΔYP. With Steel No. U in which the C content is out of the predetermined range, and consequently the area ratio of the second phase is out of the predetermined range, low YR cannot be achieved. In Steel Nos. X and Y containing large amounts of P and Si, the second phase is coarsened, but low YP cannot be achieved because the amount of solid-solution hardening is excessively increased. Therefore, with conventional steel, a steel sheet satisfying low YP, small ΔYP, and high BH cannot be obtained.
0.18
1.83
0.11
1.88
0.40
0.21
Mo: 0.28
0.006
2.15
0.30
0.14
0.60
0.035
0.25
740
830
5.0
5.0
5.0
5.0
830
40
50
15
5.0
5.0
5.0
5.0
10
10
| Number | Date | Country | Kind |
|---|---|---|---|
| 2007-181947 | Jul 2007 | JP | national |
This is a §371 of International Application No. PCT/JP2008/062873, with an international filing date of Jul. 10, 2008 (WO 2009/008548 A1, published Jan. 15, 2009), which is based on Japanese Patent Application Nos. 2007-181947, filed Jul. 11, 2007, and 2008-177468, filed Jul. 8, 2008, the subject matter of which is incorporated by reference.
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2008/062873 | 7/10/2008 | WO | 00 | 1/28/2010 |
