High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and process for producing the same

Abstract

The present invention provides a low-alloy high-purity ferritic stainless steel sheet provided with improved oxidation resistance and high-temperature strength by utilizing Sn addition in trace amounts without relying on excessive alloying of Al and Si which reduces fabricability and weldability or addition of rare elements such as Nb, Mo, W, and rare earths, and a process for producing the same. The high-purity ferritic stainless steel sheet includes C: 0.001 to 0.03%, Si: 0.01 to 2%, Mn: 0.01 to 1.5%, P: 0.005 to 0.05%, S: 0.0001 to 0.01%, Cr: 16 to 30%, N: 0.001 to 0.03%, Al: 0.05 to 3%, and Sn: 0.01 to 1% (% by mass), with the remainder being Fe and unavoidable impurities. A stainless steel slab having such steel components is heated, wherein an extraction temperature is 1100 to 1250 C., and a winding temperature after hot rolling is 650 C. or lower. A hot-rolled sheet is annealed at 900 to 1050 C., and cooled at 10 C./sec or less over a temperature range of 550 to 850 C.

Claims

1. A ferritic stainless steel sheet, consisting of, in % by mass, C: 0.001 to 0.03%, Si: 0.01 to 2%, Mn: 0.01 to 1.5%, P: 0.032% or less, S: 0.0001 to 0.01%, Cr: 16 to 30%, N: 0.001 to 0.03%, Al: 0.155 to 3%, and Sn: 0.01 to 1%, with the remainder being Fe and unavoidable impurities, and having a 0.2% proof stress of 35 MPa or more and a tensile strength of 65 Mpa or more at 800 C., and wherein the ferritic stainless steel sheet has oxidation resistance which does not cause unusual oxidation in a continuous oxidation test at 980 C. for 200 hr.

2. A ferritic stainless steel sheet, consisting of, in % by mass, C: 0.001 to 0.03%, Si: 0.01 to 2%, Mn: 0.01 to 1.5%, P: 0.032% or less, S: 0.0001 to 0.01%, Cr: 16 to 30%, N: 0.001 to 0.03%, Al: 0.055 to 3%, and Sn: 0.01 to 1%, and one or more of Nb: 0.18% or less, Ti: 0.5% or less, Ni: 0.5% or less, Cu: 0.5% or less, Mo: 0.5% or less, V: 0.5% or less, Zr: 0.5% or less, Co: 0.5% or less, Mg: 0.005% or less, B: 0.005% or less, Ca: 0.005% or less, La: 0.1% or less, Y: 0.1% or less, Hf: 0.1% or less, and REM: 0.1% or less, with the remainder being Fe and unavoidable impurities, and having a 0.2% proof stress of 35 MPa or more and a tensile strength of 65 Mpa or more at 800 C., and wherein the ferritic stainless steel sheet has oxidation resistance which does not cause unusual oxidation in a continuous oxidation test at 980 C. for 200 hr.

3. A process for producing a ferritic stainless steel sheet, comprising heating a stainless steel slab having the steel components according to claim 1 or 2, wherein an extraction temperature is 1100 to 1250 C., and a winding temperature after hot rolling is 600 C. or lower.

4. The process for producing the ferritic stainless steel sheet according to claim 3, comprising annealing the steel sheet at 900 to 1050 C., and then cooling the annealed steel sheet at 5 C./sec or less over a temperature range of 550 to 850 C.

5. The ferritic stainless steel sheet according to claim 1 or 2, wherein the C content in the steel sheet is 0.004 to 0.007%.

6. The ferritic stainless steel sheet according to claim 5, wherein the Al content in the steel sheet is more than 0.8% to 3%.

7. A process for producing a ferritic stainless steel sheet, including heating a stainless steel slab having the steel components according to claim 5, wherein an extraction temperature is 1100 to 1250 C., and a winding temperature after hot rolling is 600 C. or lower.

8. The process for producing the ferritic stainless steel sheet according to claim 7, including annealing the steel sheet at 900 to 1050 C., and then cooling the annealed steel sheet at 5 C./sec or less over a temperature range of 550 to 850 C.

9. The ferritic stainless steel sheet according to claim 1 or 2, wherein the Al content in the steel sheet is 0.155 to 1.3%.

10. A process for producing a ferritic stainless steel sheet, including heating a stainless steel slab having the steel components according to claim 9, wherein an extraction temperature is 1100 to 1250 C., and a winding temperature after hot rolling is 600 C. or lower.

11. The process for producing the ferritic stainless steel sheet according to claim 10, including annealing the steel sheet at 900 to 1050 C., and then cooling the annealed steel sheet at 5 C./sec or less over a temperature range of 550 to 850 C.

12. The ferritic stainless steel sheet according to claim 1 or 2, wherein the Al content in the steel sheet is more than 0.8% to 3%.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 illustrates the relationship between the contents of Cr, Sn, and Al and oxidation resistance of the stainless steel sheet of Example 1; and

(2) FIG. 2 illustrates the relationship between the contents of Cr, Sn, and Al and oxidation resistance of the stainless steel sheet of Example 2.

BEST MODE FOR CARRYING OUT THE INVENTION

(3) The requirements of the present invention will now be described in detail. It should be understood that % representation of the content of each element means % by mass.

(4) (I) First, limitations on the components of the steel sheet will now be described.

(5) C deteriorates oxidation resistance, and its content is preferably as small as possible; thus, the upper limit is 0.03%. However, excessive reduction leads to increased refining cost; thus, the lower limit is 0.001%. Preferably, in view of oxidation resistance and production cost, the C content is 0.002 to 0.01%.

(6) Si is not only effective as a deoxidizing element but also an element that improves oxidation resistance. To ensure the effect of a deoxidizer and the oxidation resistance of the present invention, the lower limit is 0.01%.

(7) However, excessive addition causes reduction in steel toughness and workability; thus, the upper limit is 2%. Preferably, in view of effectiveness and fabricability, the Si content is in the range of 0.05 to 1%, and more preferably 0.1 to 0.6%.

(8) Mn is an element that reduces oxidation resistance, and its content is preferably as small as possible. From the standpoint of preventing the reduction in oxidation resistance, the upper limit is 1.5%. However, excessive reduction leads to increased refining cost; thus, the lower limit is 0.01%. Preferably, in view of oxidation resistance and production cost, the Mn content is 0.05 to 0.5%.

(9) P is an element that reduces fabricability and weldability, and its content is preferably as small as possible. From the standpoint of preventing the reduction in fabricability and weldability, the upper limit is 0.05%. However, excessive reduction leads to increased refining cost; thus, the lower limit is 0.005%. Preferably, in view of production cost, the P content is 0.01 to 0.04%.

(10) S deteriorates oxidation resistance and hot workability, and its content is preferably as small as possible. Thus, the upper limit is 0.01%. However, excessive reduction leads to increased refining cost; thus, the lower limit is 0.0001. Preferably, in view of oxidation resistance and production cost, the S content is 0.0002 to 0.002%.

(11) Cr is a fundamental constituent element of the high-purity ferritic stainless steel of the present invention, and is an element essential to ensure the oxidation resistance and high-temperature strength, which are aimed at by the present invention, by adding Sn. To ensure the oxidation resistance and high-temperature strength of the present invention, the lower limit is 16.0%. The upper limit, from the standpoint of fabricability, is 30%. However, in terms of economic efficiency as compared to SUH21, the Cr content is preferably 16.0 to 22.0%. In view of performance and alloy cost, it is more preferably 16.0 to 18.0%.

(12) N deteriorates oxidation resistance similarly to C, and its content is preferably as small as possible; thus, the upper limit is 0.03%. However, excessive reduction leads to increased refining cost; thus, the lower limit is 0.001%. Preferably, in view of oxidation resistance and production cost, the N content is 0.005 to 0.015%.

(13) Al is not only an element effective as a deoxidizing element, but also an element essential to enhance the oxidation resistance aimed at by the present invention. The lower limit is not less than 0.05% in order to produce an oxidation resistance-improving effect in combination with Sn addition, and preferably more than 0.8%. The upper limit is 3.0% from the standpoint of fabricability. However, excessive addition causes deterioration in steel toughness and weldability; thus, the Al content is preferably more than 0.8% to 2.0%. In terms of economic efficiency as compared to SUH21, it is more preferably 1.0 to 2.0%.

(14) Sn is an element essential to ensure the oxidation resistance and high-temperature strength, which are aimed at by the present invention, without relying on excessive alloying of Al and Si or addition of rare elements such as Nb, Mo, W, and rare earths. To provide the oxidation resistance and high-temperature strength, which are aimed at by the present invention, the lower limit is 0.01%. The upper limit is 1.0% from the standpoint of fabricability. However, in terms of economic efficiency as compared to SUH21, the Sn content is preferably 0.1 to 0.6%. In view of performance and alloy cost, it is more preferably 0.2 to 0.5%.

(15) Nb and Ti are elements that improve oxidation resistance by the effect of stabilizing elements to fix C and N, and are added as required. Their amount, when added, is 0.03% or more, in which case the effect of each element is exerted. However, excessive addition leads to increase in alloy cost and reduction in fabricability associated with increased recrystallization temperature; thus, the upper limit of each element is 0.5%. In view of effectiveness, alloy cost, and fabricability, a preferred range of one or two of Nb and Ti is 0.05 to 0.5%. A more preferred range is 0.1 to 0.3%.

(16) Ni, Cu, Mo, V, Zr, and Co are elements that are effective for the increase in high-temperature strength by synergistic effects with Sn, and added as required. The amount of Ni, Cu, and Mo, when added, is 0.15% or more, in which case the effect of each element is exerted. The amount of V, Zr, and Co, when added, is 0.01% or more, in which case the effect of each element is exerted. However, excessive addition leads to increase in alloy cost and reduction in fabricability; thus, the upper limit of each element is 0.5%.

(17) Mg forms Mg oxide together with Al in molten steel to act as a deoxidizer, and, in addition, acts as crystallization nuclei of TiN. TiN forms solidification nuclei of ferrite phase in a solidification process and promotes crystallization of TiN, thereby forming fine ferrite phase at the solidification. By forming a fine solidified structure, surface defects due to a coarse solidified structure, such as ridging and roping of products, can be prevented, and, besides, the workability improves; therefore, Mg is added as required. The amount of Mg, when added, is 0.0001%, in which case such effects are exerted. However, when it is more than 0.005%, fabricability deteriorates; thus, the upper limit is 0.005%. Preferably, in view of fabricability, the Mg content is 0.0003 to 0.002%.

(18) B is an element that improves hot workability and secondary workability, and addition thereof to a high-purity ferritic stainless steel is effective. The amount of B, when added, is 0.0003% or more, in which case such an effect is exerted. However, excessive addition causes reduction in elongation; thus, the upper limit is 0.005%. Preferably, in view of material cost and workability, the B content is 0.0005 to 0.002%.

(19) Ca is an element that improves hot workability and steel cleanliness and added as required. The amount of Ca, when added, is 0.0003% or more, in which case such an effect is exerted. However, excessive addition leads to reduction in fabricability and reduction in oxidation resistance due to water-soluble inclusions such as CaS; thus, the upper limit is 0.005%. Preferably, in view of fabricability and oxidation resistance, the Ca content is 0.0003 to 0.0015%.

(20) Zr, La, Y, Hf, and REM may be added as required because they have effects of improving hot workability and steel cleanliness and significantly improving oxidation resistance and hot workability. Their amount, when added, is 0.001% or more, in which case the effect of each element is exerted. However, excessive addition leads to increase in alloy cost and reduction in fabricability; thus, the upper limit of each element is 0.1%. Preferably, in view of effectiveness, economic efficiency, and fabricability, the content of one or more of them is each 0.001 to 0.05%.

(21) (II) Limitations on the preferred process for producing a steel sheet will now be described.

(22) Mentioned below is a production process that is preferred for achieving the oxidation resistance and high-temperature strength equal to or higher than those of SUH21, provided that the components described in Section (I) above are contained.

(23) The steel sheet of the present invention is obtained by ingot-casting a steel having the component composition of (I) by a conventional method using a converter, electric furnace, or further secondary refiner, forming a slab (cast billet, steel billet) by the continuous casting process or steel ingot process, heating the slab in a heating furnace, hot-rolling the heated slab, and winding the hot-rolled steel sheet into a coil, alternatively, if necessary, annealing the hot-rolled sheet, and then further carrying out cold rolling, annealing, and pickling to form a cold-rolled steel sheet.

(24) In hot rolling, the extraction temperature after heating a cast billet (slab) is set at 1100 C. or higher in order to ensure the amount of scale deposition for removing inclusions which induce a scab from the cast billet surface. The amount of scale deposition is 0.1 mm or more in scale thickness. The upper limit of the extraction temperature is set at 1250 C. in order to inhibit the generation of MnS and CaS, which can be the origin of unusual oxidation, to thereby stabilize TICS. In view of the oxidation resistance aimed at by the present invention, the extraction temperature is preferably set at 1100 to 1200 C.

(25) The winding temperature after hot rolling is set at 600 C. or lower in order to ensure steel toughness and prevent internal oxide and grain boundary oxidation which can cause degradation of surface properties. When the winding temperature is higher than 600 C., precipitates containing Ti and P are likely to precipitate, which can lead to reduction in oxidation resistance. When the winding temperature is lower than 400 C., malformation of a hot-rolled steel tape can occur when water is poured after hot rolling, inducing a surface flaw at the time of coil unwinding or threading. In view of the oxidation resistance aimed at by the present invention, the winding temperature is preferably set at 500 to 600 C.

(26) After hot rolling, a single cold rolling or a plurality of cold rolling with intervening process annealing may be carried out omitting the hot-rolled sheet annealing. However, it is preferable to carry out hot-rolled sheet annealing at 900 C. or higher in order to increase high-temperature strength, which is aimed at by the present invention, by solid-solution strengthening of Nb and Ti, or Ni, Cu, and Mo, in addition to Sn and Cr. The upper limit of the temperature of the hot-rolled sheet annealing is preferably 1050 C. in view of reduction in surface properties and descaling-by-pickling property.

(27) Setting the rate of cooling the hot-rolled sheet at 10 C./sec or less over a temperature range of 550 to 850 C. is effective for improvement in high-temperature strength and oxidation resistance because grain boundary segregation of Sn and Cr is reduced to form a uniform solid solution and production of fine carbonitrides is promoted. The cooling rate is preferably 5 C./sec or less in order to promote fine precipitation. The lower limit is, but not restricted to, 0.01 C./sec in order to reduce large carbonitride.

(28) Cold rolling conditions are not particularly restricted. Final annealing after cold rolling is preferably carried out at 1000 C. or lower in view of surface properties. The lower limit is preferably 800 C. where, in the case of the steel sheet of the present invention, recrystallization is completed. The pickling method is not particularly restricted, and pickling is performed using a method commonly used in industry. Examples thereof include immersion in alkali salt bath electrolytic picking+immersion in nitric hydrofluoric acid, wherein in the electrolytic picking, neutral salt electrolysis, nitric acid electrolysis, or the like is performed.

EXAMPLES

(29) Examples of the present invention will now be described.

(30) A ferritic stainless steel including the components in Table 1 was ingot-cast, hot-rolled at a temperature of extraction from a heating furnace of 1180 to 1250 C., and wound at a temperature of 500 to 730 C. to form a hot-rolled steel sheet with a thickness of 3.0 to 6.0 mm. The hot-rolled steel sheet was annealed, and a single cold rolling or double cold rolling with intervening process annealing was carried out to produce a cold-rolled steel sheet with a thickness of 1.0 to 2.0 mm. The cold-rolled steel sheets obtained were all subjected to final annealing at a temperature of 850 to 1050 C. where recrystallization is completed.

(31) The steel components that are within the range defined in the present invention (components of the present invention) and that are without the range (comparative components) were used. For the production conditions, preferred conditions defined in the present invention (examples of the present invention) and other conditions (comparative examples) were used. Further, as a comparative steel, SUS430J1L (19% Cr-0.5% Nb), SUS436J1L (18Cr-1Mo), and SUS21 (18% Cr-3% Al) were used.

Example 1

(32) Various test pieces were collected from the steel sheets obtained, and Steels A to Q, SUS430J1L, and SUS436JL shown in Table 1 were tested as described below. The properties of the steel sheets were examined and evaluated.

(33) High-temperature strengths (TS, 0.2% PS) were determined by high-temperature tensile test using tensile test pieces with a parallel length of 40 mm and a width of 12.5 mm collected in the rolling direction. The high-temperature tensile test was carried out at 800 C. The tensile speed was 0.09 mm/min until 0.2% proof stress was reached and 3 mm/min after that.

(34) Oxidation resistances were evaluated by a continuous oxidation test in air at 980 C. for 200 hr using test pieces of 20 mm25 mm collected and subjected to wet #600 polish finishing on both surfaces and end faces. The results are shown in Table 2. The occurrence of (i) peel-off and (ii) unusual oxidation of a surface film was used as an evaluation index. (i) peel-off of a surface film was judged to have occurred when a change in hue that occurred as spots was observed, and (ii) unusual oxidation was judged to have occurred when a protective film on the surface was ruptured and a nodular oxidized shape mainly composed of Fe oxide was observed.

(35) In SUS430J1L and SUS436JL used as a comparative steel in the continuous oxidation test conditions in air at 980 C. for 200 hr, peel-off of a surface film was observed, and unusual oxidation was observed at some parts. Accordingly, the object of the present invention is a steel sheet having both such oxidation resistance that unusual oxidation does not occur in the continuous oxidation test at 980 C. for 200 hr and a high-temperature strength equal to or higher than that of the comparative steel (0.2% PS at 800 C.35 MPa, T.S55 MPa).

(36) TABLE-US-00001 TABLE 1 Steel Components of Samples (mass %) C Si Mn P S Cr N Al Sn Nb Ti Others A 0.004 0.06 0.08 0.021 0.0005 16.6 0.010 0.065 0.32 B 0.004 0.07 0.07 0.021 0.0006 16.6 0.011 0.055 0.31 0.12 0.08 B: 7 ppm C 0.004 0.20 0.08 0.022 0.0005 16.5 0.009 0.066 0.29 0.12 D 0.004 0.11 0.08 0.022 0.0005 16.7 0.009 0.066 0.33 0.15 0.05 Ni: 0.25 E 0.003 0.09 0.08 0.022 0.0005 16.7 0.009 0.075 0.33 0.16 0.07 Ni, Cu, Mo: 0.2 F 0.027 0.50 0.08 0.021 0.0005 16.8 0.010 0.155 0.32 0.18 0.15 Ni: 0.2, B: 5 ppm, Zr: 0.02 G 0.003 0.12 1.20 0.021 0.0005 18.8 0.010 0.075 0.25 La, Y: 0.1, REM: 0.05 H 0.005 0.06 0.08 0.021 0.0005 23.5 0.010 0.065 0.20 0.25 I 0.006 0.08 0.08 0.021 0.0005 16.4 0.026 0.455 0.32 0.17 0.18 V: 0.2, Zr: 0.05 J 0.003 0.12 0.08 0.021 0.0005 19.4 0.009 0.068 0.08 0.05 0.06 B, Mg: 7 ppm K 0.027 0.15 0.08 0.021 0.0005 16.2 0.010 0.065 0.57 0.07 0.06 Zr, Co: 0.05, Ca: 7 ppm 2A 0.005 0.05 0.11 0.018 0.0005 17.2 0.010 1.1 0.31 2B 0.005 0.02 0.12 0.019 0.0006 16.8 0.011 1.5 0.25 0.15 0.11 Ca: 7 ppm 2C 0.004 0.90 0.08 0.022 0.0005 17.5 0.009 0.9 0.31 0.15 2D 0.004 0.20 0.08 0.022 0.0005 17.2 0.009 1.1 0.33 0.15 0.05 Ni: 0.25, Y: 0.02 2E 0.027 0.50 0.08 0.021 0.0005 16.8 0.010 1.2 0.32 0.18 0.15 2F 0.003 0.15 1.20 0.021 0.0005 18.8 0.010 1.3 0.31 La, Hf, REM: 0.03 2G 0.005 0.09 0.08 0.021 0.0005 23.5 0.010 1.1 0.25 0.19 0.09 Co: 0.01 2H 0.006 0.03 0.08 0.021 0.0005 16.6 0.026 2.6 0.32 0.17 0.18 V, Zr: 0.05 2I 0.003 0.15 0.08 0.021 0.0005 19.4 0.009 1.2 0.08 0.05 0.06 B, Mg: 7 ppm 2J 0.007 0.17 0.08 0.021 0.0005 17.2 0.010 0.9 0.57 0.07 0.06 2K 0.021 0.35 0.28 0.032 0.0018 18.6 0.022 2.3 0.21 0.13 0.11 L 0.035 0.09 0.08 0.022 0.0006 16.3 0.015 0.075 0.25 0.19 0.09 M 0.003 0.20 1.70 0.023 0.0015 17.2 0.011 0.085 0.11 0.11 0.11 N 0.005 0.08 0.09 0.022 0.0011 15.7 0.012 0.075 0.22 0.15 O 0.003 0.18 0.11 0.023 0.0009 16.3 0.033 0.085 0.24 0.22 P 0.005 0.15 0.11 0.021 0.0006 16.4 0.011 0.042 0.21 0.21 Q 0.005 0.13 0.12 0.022 0.0011 16.6 0.013 0.065 0.008 0.15 0.05 SUS430J1L 0.006 0.20 0.30 0.023 0.0012 19.5 0.015 0.035 0.55 SUS436J1L 0.004 0.20 0.12 0.021 0.0009 17.8 0.011 0.060 0.20 Mo: 1.1 2L 0.035 0.13 0.08 0.022 0.0006 16.3 0.015 1.1 0.25 0.19 0.09 2M 0.003 0.20 1.70 0.023 0.0015 17.2 0.011 1.1 0.25 0.11 0.11 2N 0.005 0.18 0.09 0.022 0.0011 15.5 0.012 1.1 0.32 0.15 2O 0.003 0.28 0.11 0.023 0.0009 16.8 0.033 1.1 0.24 0.22 2P 0.005 0.15 0.12 0.022 0.0011 16.7 0.013 1.1 0.008 0.15 0.05 SUH21 0.008 0.21 0.11 0.033 0.0008 18.2 0.015 3.1 0.15 Note: Underlines denote outside the scope of the present invention. : No addition.

(37) TABLE-US-00002 TABLE 2 Production Conditions and Relationship between Oxidation Resistance and High-Temperature Strength High- Temperature Strength at Oxidation at 980 C. Hot-Rolled 800 C. for 200 hr Sheet Annealing (MPa) Unusual Hot Rolling ( C.) Temperature Cooling Rate No Steel 0.2% PS TS Peel-Off Oxidation Extraction Winding ( C.) ( C./sec) Remarks Components of 1 A 40 70 Not Not 1180 550 880 5 Example of the the Present Observed Observed Present Invention Invention 2 35 65 Observed Not 1180 700* 880 13* Example of the Observed Present Invention 3 35 65 Observed Not 1180 520 870 15* Example of the Observed Present Invention 4 35 65 Observed Not 1180 700* 870 5 Example of the Observed Present Invention 5 B 45 70 Not Not 1190 530 980 5 Example of the Observed Observed Present Invention 6 35 65 Observed Not 1160 720* 990 15* Example of the Observed Present Invention 7 C 35 65 Not Not 1160 550 890 10 Example of the Observed Observed Present Invention 8 D 45 75 Not Not 1160 520 990 8 Example of the Observed Observed Present Invention 9 E 50 80 Observed Not 1180 550 1000 15* Example of the Observed Present Invention 10 F 40 70 Observed Not 1180 720* 1020 3 Example of the Observed Present Invention 11 G 45 80 Not Not 1210 580 1010 5 Example of the Observed Observed Present Invention 12 H 50 85 Not Not 1240 570 1020 10 Example of the Observed Observed Present Invention 13 I 40 65 Observed Not 1120 500 970 8 Example of the Observed Present Invention 14 J 40 70 Not Not 1210 540 1020 10 Example of the Observed Observed Present Invention 15 K 35 65 Not Not 1180 520 980 5 Example of the Observed Observed Present Invention Comparative 16 L 35 70 Observed Observed 1180 520 980 5 Comparative Components Example 17 M 25* 50* Observed Observed 1190 530 980 5 Comparative Example 18 N 35 70 Observed Observed 1190 530 990 5 Comparative Example 19 O 35 70 Observed Observed 1180 520 980 5 Comparative Example 20 P 35 70 Observed Observed 1190 530 980 5 Comparative Example 21 Q 35 70 Observed Observed 1180 520 990 5 Comparative Example 22 430J1L 35 55 Observed Observed Reference Example 23 436J1L 35 50 Observed Observed Reference Example Notes: Asterisk indicates that the Example varies from the preferred production process of the present invention.

(38) Table 2 shows that Test No. 1, 5, 7, 8, and 11 to 15 are a high-purity ferritic stainless steel that satisfy both of the components defined in the present invention and the preferred production process (hot-rolling conditions, hot-rolled sheet annealing conditions). These steel sheets are provided with a high-temperature strength and oxidation resistance higher than those of SUS430J1L and 436J1L.

(39) Test No. 2, 3, 4, 6, 9, and 10 have the components defined in the present invention and vary partially and totally from the preferred production process of the present invention (hot-rolling conditions, hot-rolled sheet annealing conditions). These steel sheets, however, are provided with a high-temperature strength and oxidation resistance equal to those of SUS430J1 and SUS436J1L, which are aimed at by the present invention. Further, Test No. 13 contains a large N content compared to the steels of other inventive examples, and, although varying from the high purification suitable in the present invention, has composition within the scope of the present invention, which is the case of having the properties aimed at by the present invention.

(40) Test No. 16 to 21 implement the preferred production process of the present invention (hot-rolling conditions, hot-rolled sheet annealing conditions), but vary from the components of the present invention. These steel sheets are not provided with the high-temperature strength and oxidation resistance aimed at by the present invention.

Example 2

(41) Various test pieces were collected from the steel sheets obtained in the same manner as in Example 1, and Steels 2A to 2Q and SUS21 (18% Cr-3% Al) were tested in the same manner as in Example 1. The properties of the steel sheets were examined and evaluated.

(42) However, oxidation resistances were evaluated by a continuous oxidation test under harsher conditions in air at 1050 C. for 200 hr. The results are shown in Table 3. The occurrence of (i) peel-off and (ii) unusual oxidation of a surface film was used as an evaluation index, similarly to Example 1. (i) peel-off of a surface film was judged to have occurred when a change in hue that occurred as spots was observed, and (ii) unusual oxidation was judged to have occurred when a protective film on the surface was ruptured and a nodular oxidized shape mainly composed of Fe oxide was observed.

(43) In SUH21 (18Cr-3Al) used as a comparative steel, if not unusual oxidation, change in hue and peel-off associated therewith of a surface film was partially observed. Accordingly, the object of the present invention is a steel sheet having both such oxidation resistance that unusual oxidation does not occur in the continuous oxidation test in air at 1050 C. for 200 hr and a high-temperature strength equal to or higher than that of the comparative steel (0.2% P.S at 800 C.45 MPa, T.S60 MPa).

(44) TABLE-US-00003 TABLE 3 Production Conditions and Relationship between Oxidation Resistance and High-Temperature Strength High- Temperature Strength at Oxidation at 1050 C. Hot-Rolled 800 C. for 200 hr Sheet Annealing (MPa) Unusual Hot Rolling ( C.) Temperature Cooling Rate No Steel 0.2% PS TS Peel-Off Oxidation Extraction Winding ( C.) ( C./sec) Remarks Components of 21 2A 40 70 Not Not 1210 540 890 5 Example of the the Present Observed Observed Present Invention Invention 22 35* 55* Observed Not 1230 700* 880 15* Example of the Observed Present Invention 23 2B 45 80 Not Not 1230 550 990 5 Example of the Observed Observed Present Invention 24 40 70 Observed Not 1210 730* 970 15 Example of the Observed Present Invention 25 2C 50 70 Not Not 1210 560 890 10 Example of the Observed Observed Present Invention 26 2D 50 80 Not Not 1230 550 1000 8 Example of the Observed Observed Present Invention 27 2E 50 85 Observed Not 1210 580 980 15* Example of the Observed Present Invention 28 50 85 Observed Not 1210 580 980 5 Example of the Observed Present Invention 29 2F 55 90 Not Not 1230 520 1020 5 Example of the Observed Observed Present Invention 30 2G 55 90 Not Not 1240 580 1010 5 Example of the Observed Observed Present Invention 31 2H 50 85 Not Not 1240 570 1020 10 Example of the Observed Observed Present Invention 32 2I 50 85 Not Not 1230 500 970 8 Example of the Observed Observed Present Invention 33 2J 55 100 Not Not 1210 540 1020 10 Example of the Observed Observed Present Invention 34 2K 60 95 Observed Not 1210 550 990 5 Example of the Observed Present Invention Comparative 35 2L 45 75 Observed Observed 1180 520 980 5 Comparative Components Example 36 2M 40 75 Observed Observed 1190 530 980 5 Comparative Example 37 2N 45 75 Observed Observed 1190 530 990 5 Comparative Example 38 2O 45 75 Observed Observed 1180 520 980 5 Comparative Example 39 2P 35* 55* Observed Observed 1190 530 980 5 Comparative Example 40 2Q 40 65 Observed Observed 1190 520 980 5 Comparative Example 41 SUS21 40 60 Observed Not Reference Example Observed Notes: Asterisk indicates that the Example varies from the preferred production process of the present invention.

(45) Table 3 shows that Test No. 21, 23, 25, 26, and 29 to 33 are a high-purity ferritic stainless steel that satisfy both of the components defined in the present invention and the preferred production process (hot-rolling conditions, hot-rolled sheet annealing conditions). These steel sheets had an alumina film and exhibited an oxidation resistance equal to or higher than that of the comparative steel SUS21, and achieved the high-temperature strength at the same time.

(46) Test No. 22, 24, and 27 have the components defined in the present invention and vary partially and totally from the preferred production process of the present invention (hot-rolling conditions, hot-rolled sheet annealing conditions). These steel sheets, however, are provided with a high-temperature strength and oxidation resistance equal to those of SUS21, which are aimed at by the present invention. Further, Test No. 28, 31, and 34 contain a large N content compared to the steel of other inventive examples, and, although varying from the high purification suitable in the present invention, have composition within the scope of the present invention, which is the case of having the properties aimed at by the present invention. Test No. 11 and 14 are provided with the high-temperature strength and oxidation resistance aimed at by the present invention, but they have an Al content of more than 2% and are slightly poor in weldability and toughness among the examples of the present invention.

(47) Test No. 35 to 40 implement the preferred production process of the present invention (hot-rolling conditions, hot-rolled sheet annealing conditions), but vary from the components of the present invention. These steel sheets are not provided with the high-temperature strength and oxidation resistance aimed at by the present invention.

(48) FIG. 1 illustrates the relationship between the contents of Cr, Sn, and Al of the steel of Example 1 shown in Table 1 and the oxidation resistance shown in Table 2. Similarly, FIG. 2 illustrates the relationship between the contents of Cr, Sn, and Al of the steel of Example 2 shown in Table 1 and the oxidation resistance shown in Table 3. The steels provided with the oxidation resistance aimed at by the present invention are denoted by , and the steels whose oxidation resistance was evaluated to be equal to or lower than that of comparative steels by . The results shows that for obtaining good oxidation resistance as well as high-temperature strength by adding Sn, it is important to adjust to be in the component range defined in the present invention (Cr, Sn, Al).

INDUSTRIAL APPLICABILITY

(49) According to the present invention, a low-alloy high-purity ferritic stainless steel sheet provided with improved oxidation resistance and high-temperature strength equal to or higher than those of existing heat-resistant steels by utilizing Sn addition in trace amounts can be obtained without relying on excessive alloying of Al and Si which reduces fabricability and weldability or addition of rare elements such as Nb, Mo, W, and rare earths.