JPWO2014087648A1 - Ferritic stainless steel sheet - Google Patents

Abstract

A ferritic stainless steel sheet is provided. C: 0.004% to 0.014%, N: 0.004% to 0.014%, Si: 0.01% to 0.30%, Mn: 0.01% or more 0.30% or less, P: 0.025% or more and 0.040% or less, S: 0.010% or less, Al: 0.01% or more and 0.08% or less, Cr: 10.5% or more and 24.0 %: Ni: 0.01% or more and 0.40% or less, Ti: 0.20% or more and 0.38% or less, Nb: 0.012% or less, O: 0.0060% or less, and ( (P% + S% + 10 × O%) × Ti% ≦ 0.025 in a range satisfying P, S, O, Ti, the balance being made of Fe and inevitable impurities . P%, S%, 0%, and Ti% represent the contents (mass%) of P, S, O, and Ti, respectively.

Description

  The present invention relates to a ferritic stainless steel sheet, and more particularly to a ferritic stainless steel sheet having excellent surface properties.

  Stainless steel sheets are roughly classified into ferritic stainless steel sheets represented by SUS430 and austenitic stainless steel sheets represented by SUS304. Ferritic stainless steel sheets have a smaller thermal expansion coefficient and higher thermal conductivity than austenitic stainless steel sheets. For this reason, a ferritic stainless steel sheet is excellent in thermal fatigue resistance. In addition, stress corrosion cracking resistance is less likely to occur. Ferritic stainless steel sheets with these properties are used in automotive exhaust system components that require excellent thermal fatigue properties in addition to heat resistance and oxidation resistance, and excellent stress corrosion cracking resistance. It is applied to kitchen facilities and electric water heaters that require high power. Furthermore, compared to austenitic stainless steel sheets, ferritic stainless steel sheets have the great advantage that they can be manufactured at a low cost because they contain less expensive elements such as Ni and Mn, which are austenite former elements. Have. These excellent properties have been evaluated, and ferritic stainless steel sheets have been applied to various applications, and their needs have been increasing in recent years.

  By the way, excellent surface properties are required for applications requiring cleanliness and design. Therefore, the ferritic stainless steel sheet applied for such applications is required to have not only the above properties but also excellent surface properties.

  For example, Patent Document 1 discloses a technique for reducing the generation of TiN inclusions by regulating the amounts of Ti, N, and O to deal with such problems. As described above, there are a large number of disclosure examples regarding techniques for avoiding the generation of oxides or nitrides of transition metals such as Ti. However, even if these regulations are performed, the surface texture may deteriorate, and an excellent surface texture cannot be obtained only by component regulation considering only oxides and nitrides.

JP 2002-275590 A

  The present invention has been made to solve the above-described problems, and an object thereof is to provide a ferritic stainless steel sheet having excellent surface properties.

  The present inventors investigated the types of inclusions produced in the ferritic stainless steel sheet and the amounts produced. As a result, on the steel sheet surface, in addition to Ti-based oxides conventionally considered, coarse Ti-based sulfides and Ti-based phosphides (Ti-based oxides) Phosphide) was also produced, and it was revealed that this coarse Ti-based sulfide and phosphide deteriorated the surface properties of the steel sheet.

  Then, next, the present inventors diligently studied the steel plate component range in which the surface properties are not deteriorated by Ti-based oxides, sulfides and phosphides. As a result, it has been found that by appropriately managing the amounts of Ti, S, P and O, the formation of the inclusions can be suppressed, and the surface properties of the steel sheet are greatly improved.

The present invention has been made based on the above findings, and the gist thereof is as follows.
[1] By mass%, C: 0.004% to 0.014%, N: 0.004% to 0.014%, Si: 0.01% to 0.30%, Mn: 0.00. 01% to 0.30%, P: 0.025% to 0.040%, S: 0.010% or less, Al: 0.01% to 0.08%, Cr: 10.5% or more 24.0% or less, Ni: 0.01% or more and 0.40% or less, Ti: 0.20% or more and 0.38% or less, Nb: 0.012% or less, O: 0.0060% or less, And, it contains P, S, O, Ti in a range satisfying (P% + S% + 10 × O%) × Ti% ≦ 0.025, and the balance is made of Fe and inevitable impurities. Ferritic stainless steel sheet. The P%, the S%, the O%, and the Ti% represent the contents (mass%) of P, S, O, and Ti, respectively.
[2] By mass%, Cu: 0.01% to 0.48%, Mo: 0.01% to 1.20%, V: 0.01% to 0.10% The ferritic stainless steel sheet according to [1] above, which contains one or more selected.
[3] By mass%, Zr: 0.01% to 0.20%, REM: 0.001% to 0.100%, W: 0.01% to 0.20%, Co: 0.01% or more and 0.20% or less, B: 0.0002% or more and 0.0020% or less, Mg: 0.0002% or more and 0.0010% or less, Ca: 0.0005% or more and 0.0030% or less The ferritic stainless steel sheet according to [1] or [2] above, containing one or more selected from among them.

  According to the present invention, a ferritic stainless steel sheet having excellent surface properties can be obtained.

  The present invention provides a technology for obtaining a ferritic stainless steel sheet having excellent surface properties by effectively suppressing the formation of Ti-based sulfides and phosphides, which have not been considered in the past, in addition to Ti-based oxides. About. The reason which prescribed | regulated the component composition of the steel plate of this invention below is demonstrated. In addition, all the component% means the mass% unless there is particular notice.

C: 0.004% or more and 0.014% or less When the amount of C exceeds 0.014%, the workability is deteriorated and the corrosion resistance of the welded part is significantly lowered when welding is performed. A lower C content is preferable from the viewpoint of corrosion resistance and workability. However, in order to make the amount of C less than 0.004%, it is necessary to lengthen the refining time, which is not preferable in production. For this reason, the C content is in the range of 0.004% to 0.014%. Preferably it is 0.004% or more and 0.011% or less of range. More preferably, it is 0.005% or more and 0.008% or less of range.

N: 0.004% or more and 0.014% or less When the N amount exceeds 0.014%, the workability is deteriorated and the corrosion resistance of the welded part is significantly lowered when welding is performed. From the viewpoint of corrosion resistance, the N content is preferably as low as possible. However, in order to reduce the amount of N to less than 0.004%, it is necessary to lengthen the refining time, which causes an increase in manufacturing cost and a decrease in productivity, which is not preferable. Therefore, the N amount is set in the range of 0.004% to 0.014%. Preferably it is 0.004% or more and 0.011% or less of range. More preferably, it is 0.006% or more and 0.009% or less of range.

Si: 0.01% or more and 0.30% or less Si is an element useful as a deoxidizer in the steelmaking process. This effect can be obtained by making the Si amount 0.01% or more. The effect increases as the Si amount increases. However, if the amount of Si exceeds 0.30%, the rolling load in the hot rolling process increases and the productivity decreases, and a large amount of oxide scale is generated on the surface, resulting in an increase in surface defects. Therefore, it is not preferable. Therefore, the Si amount is set to 0.01% or more and 0.30% or less. In order to perform descaling more easily in the annealing / pickling process, the Si content is preferably 0.25% or less. More preferably, it is 0.20% or less.

Mn: 0.01% or more and 0.30% or less Mn has an effect of increasing the strength of the steel sheet, and is also an element useful as a deoxidizer. In order to acquire these effects, it is necessary to make Mn amount 0.01% or more. However, if the amount of Mn exceeds 0.30%, the thickness of the oxide scale generated in the annealing process of the hot-rolled sheet or the annealing process of the cold-rolled sheet becomes thick, and the surface properties are lowered. Therefore, the amount of Mn is 0.01% or more and 0.30% or less. Preferably it is 0.05 to 0.25% of range. More preferably, it is 0.05 to 0.20% of range.

P: 0.025% or more and 0.040% or less P is an element inevitably contained in the steel sheet. Further, excessive P content reduces weldability and easily causes intergranular corrosion. This tendency becomes remarkable when the amount of P exceeds 0.040%. A lower P content is preferable from the viewpoint of weldability and prevention of intergranular corrosion. However, in order to make the P amount less than 0.025%, it is necessary to lengthen the refining time, which is not preferable in production. Therefore, the P content is in the range of 0.025% to 0.040%. Preferably, it is 0.025% or more and 0.035% or less. More preferably, it is 0.025% or more and 0.030% or less.

S: 0.010% or less S, like P, is an element inevitably contained in the steel sheet. When the amount of S exceeds 0.010%, the corrosion resistance decreases. Therefore, the S amount is 0.010% or less. Preferably it is 0.007% or less. More preferably, it is 0.004% or less.

Al: 0.01% or more and 0.08% or less Al is an effective deoxidizer. This effect as a deoxidizer can be obtained by making the Al content 0.01% or more. However, if the amount of Al exceeds 0.08%, surface defects due to Al-based inclusions may occur, and pickling properties in the annealing process are deteriorated, which is not preferable in production. Therefore, the Al content is set in a range of 0.01% to 0.08%. Preferably it is 0.01% or more and 0.06% or less of range. More preferably, it is 0.02% or more and 0.05% or less.

Cr: 10.5% or more and 24.0% or less Cr is the most important element for securing the corrosion resistance of the stainless steel plate. If the Cr content is less than 10.5%, sufficient corrosion resistance cannot be obtained. On the other hand, if the amount of Cr exceeds 24.0%, the toughness of the hot-rolled sheet decreases due to the generation of the sigma phase, and continuous annealing of the hot-rolled sheet becomes difficult, which is not preferable in production. Therefore, the Cr content is in the range of 10.5% or more and 24.0% or less. Preferably it is 12.0% or more and 24.0% or less of range. More preferably, it is 15.0% or more and 21.5% or less of range. Even more preferably, it is in the range of 16.0% or more and 19.0% or less.

Ni: 0.01% or more and 0.40% or less Ni is an element that improves the corrosion resistance of stainless steel sheets, and the progress of corrosion in a corrosive environment where a passive film cannot be formed and active dissolution occurs. It is an element which suppresses. This effect is obtained by setting the Ni content to 0.01% or more, and increases as the Ni content increases. However, when the Ni content exceeds 0.40%, workability is lowered and stress corrosion cracking is likely to occur. Furthermore, since Ni is an expensive element, an increase in the amount of Ni causes an increase in manufacturing cost, which is not preferable. Therefore, the Ni content is 0.01% or more and 0.40% or less. Preferably it is 0.05 to 0.30% of range. More preferably, it is 0.10% or more and 0.20% or less of range.

Ti: 0.20% or more and 0.38% or less Ti combines with C or N to improve workability or prevent the weld from becoming sensitized and improve the corrosion resistance of the weld. In order to obtain this effect, the Ti amount needs to be 0.20% or more. However, if the amount of Ti exceeds 0.38%, coarse Ti carbonitride is generated in the casting process and causes surface defects, which is not preferable. Therefore, the Ti amount is set to 0.20% or more and 0.38% or less. Preferably it is 0.20% or more and 0.35% or less of range. More preferably, it is 0.25% or more and 0.35% or less of range.

Nb: 0.012% or less If the Nb content exceeds 0.012%, the recrystallization temperature rises, and good mechanical properties are achieved unless the annealing temperature of the hot-rolled sheet or the annealing temperature of the cold-rolled sheet is increased. Cannot be obtained. When these annealing temperatures are raised, the scale generated during annealing becomes thicker. Therefore, some scales remain after pickling, or the surface is roughened by performing strong pickling to remove thick scales, and the surface properties are deteriorated. Therefore, the Nb content is 0.012% or less. Preferably it is 0.008% or less. More preferably, it is 0.005% or less.

O: 0.0060% or less O is an element that improves the penetration depth during welding. However, if the amount of O exceeds 0.0060%, the amount of oxide inclusions increases and the corrosion resistance decreases. Therefore, the O amount is set to 0.0060% or less. Preferably it is 0.0045% or less. More preferably, it is 0.0030% or less.

(P% + S% + 10 × O%) × Ti% ≦ 0.025
Ti forms inclusions with P, S and O. When (P% + S% + 10 × O%) × Ti% exceeds 0.025, the amount of Ti-based inclusions generated on the steel sheet surface increases and the inclusions become coarse, resulting in a decrease in surface defects and surface gloss. Since surface quality deteriorates, it is not preferable. Further, if (P% + S% + 10 × O%) × Ti% exceeds 0.025, it is preferable because coarse Ti-based inclusions generated on the surface of the steel sheet cause defects in the passive film and lower the corrosion resistance. Absent.
Therefore, (P% + S% + 10 × O%) × Ti% is set to 0.025 or less. P%, S%, 0%, and Ti% represent the contents (mass%) of P, S, O, and Ti, respectively.

  From the above, the ferritic stainless steel sheet of the present invention contains the above essential components, with the balance being Fe and unavoidable impurities.

  Moreover, the ferritic stainless steel sheet of the present invention is further optionally selected from one or more selected from Cu, Mo and V, and from Zr, REM, W, Co, B, Mg and Ca. 1 type (s) or 2 or more types selected can be contained within the following range.

One or more of Cu, Mo, and V Cu: 0.01% or more and 0.48% or less Cu is an element that improves corrosion resistance. Cu is an element particularly effective for improving the corrosion resistance of the base material and the weld when the steel plate is in an aqueous solution or when weakly acidic water droplets adhere to the steel plate. This effect is obtained by making Cu 0.01% or more, and the effect becomes higher as the amount of Cu increases. However, when the amount of Cu exceeds 0.48%, hot workability is deteriorated, and an oxide derived from Cu called red scale is formed on the slab during hot rolling, resulting in surface defects. Therefore, it is not preferable. Furthermore, since descaling after annealing becomes difficult, it is not preferable in production. Therefore, when adding Cu, the amount of Cu shall be 0.01% or more and 0.48% or less. Preferably, it is 0.10% or more and 0.48% or less of range. More preferably, it is 0.30% or more and 0.45% or less of range.

Mo: 0.01% or more and 1.20% or less Mo is an element that remarkably improves the corrosion resistance of the stainless steel plate. This effect is obtained by setting the Mo amount to 0.01% or more, and the effect increases as the Mo amount increases. However, if the Mo content exceeds 1.20%, the hot workability is deteriorated and surface defects frequently occur during hot rolling. Moreover, since Mo is an expensive element, the addition of a large amount increases the manufacturing cost. Therefore, when adding Mo, the amount of Mo shall be 0.01% or more and 1.20% or less. Preferably it is 0.30% or more and 1.20% or less of range. More preferably, it is 0.30% or more and 0.90% or less of range. More preferably, it is 0.40% or more and 0.60% or less of range.

V: 0.01% or more and 0.10% or less V is an element effective for refining crystal grains after annealing, preventing surface deteorations and improving fatigue characteristics. Further, V is combined with C or N and has an effect of suppressing a decrease in corrosion resistance due to the sensitization of the welded portion. These effects can be obtained by making the V amount 0.01% or more. However, if the V amount exceeds 0.10%, the workability is lowered and the raw material cost is increased, which is not preferable. Therefore, when adding V, the amount of V is made 0.01% or more and 0.10% or less. Preferably it is 0.01% or more and 0.07% or less of range. More preferably, it is 0.02% or more and 0.05% or less.

One or more selected from Zr, REM, W, Co, B, Mg, Ca Zr: 0.01% or more and 0.20% or less Zr combines with C and N to sensitize welds Has the effect of increasing the high temperature strength. These effects can be obtained by making the amount of Zr 0.01% or more. On the other hand, if the amount of Zr exceeds 0.20%, workability deteriorates. Moreover, since Zr is an expensive element, excessive addition causes an increase in manufacturing cost, which is not preferable. Therefore, when adding Zr, the amount of Zr shall be 0.01% or more and 0.20% or less. Preferably, the range is 0.01% or more and 0.10% or less.

REM: 0.001% or more and 0.100% or less REM has the effect of improving oxidation resistance, and in particular, suppresses the formation of an oxide film on the weld and improves the corrosion resistance of the weld. effective. In order to obtain this effect, the REM amount needs to be 0.001% or more. On the other hand, if the amount of REM exceeds 0.100%, the hot rollability deteriorates and surface defects frequently occur, which is not preferable. Therefore, when adding REM, the amount of REM shall be 0.001% or more and 0.100% or less. Preferably, it is set as 0.001% or more and 0.050% or less of range.

W: 0.01% or more and 0.20% or less W, like Mo, has the effect of improving the corrosion resistance. This effect can be obtained by making the W amount 0.01% or more. On the other hand, if the amount of W exceeds 0.20%, the strength increases, and the productivity is lowered due to an increase in rolling load or the like, which is not preferable. For this reason, when W is added, the W content is in the range of 0.01% to 0.20%. Preferably, the range is 0.01% or more and 0.10% or less.

Co: 0.01% or more and 0.20% or less Co is an element that improves toughness. This effect can be obtained by making the Co content 0.01% or more. On the other hand, if the amount of Co exceeds 0.20%, workability deteriorates. Therefore, when adding Co, the amount of Co is set to a range of 0.01% or more and 0.20% or less. Preferably, the range is 0.01% or more and 0.10% or less.

B: 0.0002% or more and 0.0020% or less B is an element effective for improving resistance to secondary working embrittlement after deep drawing. This effect can be obtained by making the B amount 0.0002% or more. On the other hand, if the amount of B exceeds 0.0020%, the rolling load during hot rolling increases and surface defects increase, which is not preferable. Therefore, when adding B, the amount of B is made into the range of 0.0002% or more and 0.0020% or less. Preferably it is 0.0005% or more and 0.0015% or less of range.

Mg: 0.0002% or more and 0.0010% or less Mg is an element that improves the rate of equiaxed crystals of the slab and is effective in improving workability and toughness. Furthermore, in a steel sheet containing Ti as in the present invention, the toughness decreases when the Ti carbonitride becomes coarse, but Mg also has an effect of suppressing the coarsening of the Ti carbonitride. These effects can be obtained by setting the Mg amount to 0.0002% or more. On the other hand, if the amount of Mg exceeds 0.0010%, the amount of Mg inclusions increases and the surface properties of the steel sheet are deteriorated. Therefore, when adding Mg, the amount of Mg is set in the range of 0.0002% to 0.0010%. Preferably it is 0.0002% or more and 0.0004% or less of range.

Ca: 0.0005% or more and 0.0030% or less Ca is an effective component for preventing the choke of nozzle due to precipitation of Ti inclusions which are likely to occur during continuous casting. The effect is acquired by making Ca amount 0.0005% or more. However, if the Ca content exceeds 0.0030%, the corrosion resistance decreases due to the formation of CaS. Therefore, when Ca is added, the Ca content is in the range of 0.0005% to 0.0030%. Preferably it is 0.0005% or more and 0.0020% or less of range. More preferably, it is 0.0005% or more and 0.0015% or less of range.

  Next, the manufacturing method of the ferritic stainless steel plate of this invention is demonstrated.

  The ferritic stainless steel sheet of the present invention is prepared by melting a molten steel having the above composition by a known method such as a converter, an electric furnace, a vacuum melting furnace, and the like, and a continuous casting method or an ingot and blooming method (ingot and bloomig method ) Steel material (slab). This slab is heated at 1100 to 1250 ° C. for 1 to 24 hours, or directly hot-rolled as cast without heating to obtain a hot-rolled sheet.

  Usually, a hot-rolled sheet is subjected to continuous annealing at 800 to 1100 ° C. and annealing of a hot-rolled sheet by batch annealing at 700 to 900 ° C. In addition, you may abbreviate | omit a hot-rolled sheet depending on a use. Next, the hot-rolled sheet after annealing or the unrolled hot-rolled sheet is subjected to pickling and cold rolling to become a cold-rolled sheet. Thereafter, the cold-rolled sheet is annealed and pickled to become a product.

  Cold rolling is preferably performed at a rolling reduction of 50% or more from the viewpoints of ductility, bendability, press formability, and leveling.

  In general, the recrystallization annealing of a cold-rolled sheet is performed according to JIS G 0203 surface finish, No. In the case of a 2B finished product, it is preferable to carry out at 800 to 1000 ° C. from the viewpoint of obtaining good mechanical properties and pickling properties. Further, BA annealing (bright annealing) may be performed in order to obtain more gloss.

  In addition, in order to further improve the surface properties after cold rolling and after processing, grinding or polishing may be performed.

  Hereinafter, the present invention will be described in more detail based on examples.

  A stainless steel plate having a chemical composition shown in Table 1 (essential components are shown in Table 1-1 and optional components are shown in Table 1-2) was melted in a 50 kg small vacuum melting furnace. These steel ingots were heated to 1150 ° C. and then hot-rolled to obtain 3.5 mm thick hot rolled sheets. Subsequently, the hot-rolled sheet obtained above was annealed at 950 ° C. for 10 minutes, then shot blasted, pickled with a mixed acid of hydrofluoric acid and nitric acid, and cold-rolled to a thickness of 0.8 mm. Cold-rolled sheet was used. The obtained cold-rolled sheet was subjected to finish annealing at 900 ° C. in an air atmosphere, and then pickled with a mixed acid of hydrofluoric acid and nitric acid.

  The cold-rolled annealed pickling plate obtained as described above was subjected to surface inspection by visual observation and evaluation of corrosion resistance by a salt spray cyclic corrosion test. In the salt spray cycle test, salt spray (5% NaCl, 35 ° C., spray 2 h) → dry (60 ° C., 4 h, relative humidity 40%) → wet (50 ° C., 2 h, relative humidity ≧ 95%) is one cycle. Five cycles were performed.

  In the surface inspection by visual observation, the case where the surface defect area was less than 5% was regarded as acceptable. In the salt spray cycle test, the case where no corrosion occurred after the end of 5 cycles was regarded as acceptable. When both the surface inspection and the salt spray cycle test passed, it was determined that a predetermined material was obtained.

  The results obtained as described above are shown in Table 2.

  From Table 2, in the invention examples A1 to A18, surface defects were not recognized, and corrosion was not generated even in the salt spray cycle test, and good surface quality was obtained.

  On the other hand, in Comparative Example B1 in which the Cr content is below the range of the present invention, a predetermined surface quality was obtained, but corrosion occurred on the entire surface of the test piece in the salt spray cycle test, and sufficient corrosion resistance was not obtained.

  In Comparative Example B2 in which Cr was added beyond the scope of the present invention, the test was not carried out because the hot-rolled sheet was poor in toughness and cracking occurred in the next cold rolling process.

  In Comparative Example B3 in which Ti was added beyond the scope of the present invention, surface defects (streak-like flaw) caused by coarse Ti carbonitride occurred.

  In Comparative Examples B4 to B7 in which (P% + S% + 10 × O%) × Ti%, P, S, or O exceeds the range of the present invention, a large amount of coarse Ti-based inclusions were generated in the steel sheet surface layer portion. Due to surface defects (scrab, linear scdab, etc.), predetermined surface quality could not be obtained.

  Further, in Comparative Examples B8 and B9 in which Si or Al was added beyond the range of the present invention, the scale could not be completely removed by pickling, and some scale remained, and a good surface appearance could not be obtained. It was. In the salt spray cycle test, corrosion occurred from the remaining scale that could not be removed by pickling.

  From the above results, in addition to the definition of the content of each element, the value of (P% + S% + 10 × O%) × Ti% ≦ 0.025 is appropriately adjusted within the scope of the present invention, so that the surface properties It was confirmed that an excellent ferritic stainless steel sheet was obtained.

  Since the ferritic stainless steel plate obtained by the present invention has excellent surface quality, it is suitable for use in automobile parts such as building materials and molding materials.

Claims (3)

C: 0.004% to 0.014%, N: 0.004% to 0.014%, Si: 0.01% to 0.30%, Mn: 0.01% or more 0.30% or less, P: 0.025% or more and 0.040% or less, S: 0.010% or less, Al: 0.01% or more and 0.08% or less, Cr: 10.5% or more and 24.0 %: Ni: 0.01% or more and 0.40% or less, Ti: 0.20% or more and 0.38% or less, Nb: 0.012% or less, O: 0.0060% or less, and
(P% + S% + 10 × O%) × Ti% ≦ 0.025 is contained, P, S, O, Ti is contained, and the balance is made of Fe and inevitable impurities. steel sheet. The P%, the S%, the 0%, and the Ti% represent the contents (mass%) of P, S, O, and Ti, respectively.   1% selected from Cu: 0.01% to 0.48%, Mo: 0.01% to 1.20%, and V: 0.01% to 0.10%. The ferritic stainless steel sheet according to claim 1, comprising seeds or two or more kinds.   Further, Zr: 0.01% to 0.20%, REM: 0.001% to 0.100%, W: 0.01% to 0.20%, Co: 0.01 %: 0.202% or less, B: 0.0002% or more and 0.0020% or less, Mg: 0.0002% or more and 0.0010% or less, Ca: 0.0005% or more and 0.0030% or less The ferritic stainless steel sheet according to claim 1, wherein the ferritic stainless steel sheet contains at least one kind selected from the above.