AU2011286685A1

AU2011286685A1 - Ferritic stainless steel

Info

Publication number: AU2011286685A1
Application number: AU2011286685A
Authority: AU
Inventors: Tooru Matsuhashi; Michio Nakata
Original assignee: Nippon Steel and Sumikin Stainless Steel Corp
Current assignee: Nippon Steel Stainless Steel Corp
Priority date: 2010-08-06
Filing date: 2011-08-04
Publication date: 2013-02-28
Also published as: EP2602351A4; JP2012036444A; US20130129560A1; TWI526549B; TW201213559A; JP5793283B2; KR20130034042A; WO2012018074A1; CN103052731A; EP2602351B1; EP2602351A1

Abstract

A ferritic stainless steel which comprises, in mass%, 0.020% or less of C, 0.025% or less of N, 1.0% or less of Si, 1.0% or less of Mn, 0.035% or less of P, 0.01% or less of S, 16.0-25.0% of Cr, 0.12% or less of Al, 0.05-0.35% of Ti, 0.0015% or less of Ca, and a remainder made up by Fe and unavoidable impurities and fulfills a requirement represented by formula (1), and in which little blackspots are produced in a welded part. BI = 3Al+Ti+0.5Si+200Ca ≤ 0.8 (1) (In formula (1), Al, Ti, Si, Ca respectively represent the contents [mass%] of these components in the steel.)

Description

DESCRIPTION FERRITIC STAINLESS STEEL TECHNICAL FIELD [0001] The present invention relates to a ferritic stainless steel that generates only a small amount of black spots in the TIG weld zone. Priority is claimed on Japanese Patent Application No. 2010-177998 filed on August 6, 2010, the content of which is incorporated herein by reference. BACKGROUND ART [0002] Ferritic stainless steel generally has properties such as a small expansion coefficient relative to the austenitic stainless steel and excellent resistance to stress corrosion cracking in addition to excellent corrosion resistance. Therefore, the ferritic stainless steel is widely used in tableware, kitchen equipment, building exterior materials such as roof materials, water or hot water container materials or the like. Further, there is increasing demand for replacement of austenitic stainless steel due to recent increasing price of nickel raw material, and the uses of ferritic stainless steel have expanded. [0003] Welding is an inevitable process in forming the above-described structure of stainless steel. Originally, ferritic stainless steel included a problem of sensitization in weld zone resulting in reduction of corrosion resistance due to the small solid-solubility limit of C and N. In order to solve the above-described problem, there has been proposed and widely practicalized a method of suppressing the sensitization of a weld metal zone by reduction of C and N contents, or by fixing of C and N by addition of stabilizing elements such as Ti and Nb, or the like (for example, see Patent Reference 1). [00041 The following have been known with regards to the corrosion resistance of weld zone in the ferritic stainless steel. Corrosion resistance is deteriorated in the scale portion generated by heat input during the welding, and therefore, it is important to perform sufficient shielding with an inert gas compared to the austenitic stainless steel. Patent Reference 2 discloses a technique of adding Ti and Al such that the formula, P1=5Ti+20(Al-0.01) > 5 (wherein Ti and Al in the formula denote amounts of respective elements in the steel) is satisfied, thereby forming an Al oxide film on the surface portion of the steel during welding to improve corrosion resistance of the weld-heat affected zone. [00051 Patent Reference 3 discloses a technique of improving crevice corrosion resistance of the weld zone by adding a certain amount or more of Si in addition to combined addition of Al and Ti. Patent Reference 4 discloses a technique to improve the corrosion resistance of a weld zone by satisfying 4A1 + Ti 0.32 (wherein each of Ti and Al denotes amount of each component in the steel), thereby reducing heat input during the welding and suppressing generation of scale in the weld zone, and improving corrosion resistance of the weld zone. The above-described prior arts have objects of improving corrosion resistance of the weld zone and weld heat affected zone. [00061 In another method, there is a technique to improve the weather resistance and crevice corrosion resistance of not the weld zone but the material itself by intentionally adding P and appropriate amounts of Ca and Al (for example, see Patent Reference 5). In Patent Reference 5, Ca and Al are added to control the shapes and distribution of non-metallic inclusions in the steel. The most important feature of Patent Reference 5 is the addition of P in excess of 0.04%, and Patent Reference 5 describes nothing about an effect during welding. Prior Art Reference Patent Reference [00071 Patent Reference 1: Japanese Examined Patent Application, Second Publication No. S55-21102. Patent Reference 2: Japanese Unexamined Patent Application, First Publication No. H05-70899 Patent Reference 3: Japanese Unexamined Patent Application, First Publication No. 2006-241564 Patent Reference 4: Japanese Unexamined Patent Application, First Publication No. 2007-270290 Patent Reference 5: Japanese Unexamined Patent Application, First Publication No. H07-34205 SUMMARY OF THE INVENTION Problems to be solved by the invention [00081 In the conventional ferritic stainless steel, dark spots (so called black spots or slag spots) occasionally occurred on the surfaces of back beads after the welding even though shielding conditions in the weld zone were controlled appropriately. Elements such as Al, Ti, Si, Ca have a strong affinity to oxygen. Black spots are oxides of these elements that are solidified on the surface of the weld metal during the solidification process of the weld metal formed by Tungsten Inert Gas (TIG) welding. Weld conditions, especially the conditions of shielding with the inert gas have a strong influence on the generation of the black spots. Many black spots occur where the shielding is insufficient.

[00091 Since the black spot itself is an oxide, there is no problem in corrosion resistance and workability of the weld zone even when the weld zone is dotted with a small amount of black spots. However, where the black spots are generated in a large amount or generated in a continuously linked manner, the appearance of the weld material used without polishing the weld zone is worsened. In addition, exfoliation of the black spots portion occasionally occurs during working of the weld zone. Where the black spot portion is exfoliated, problems such as deterioration of workability and/or occurrence of crevice corrosion in the interstitial area between the weld metal and the exfoliated black spots occasionally occur. Even when the steel member is not worked after the welding, where a thick portion is formed by the black spots, exfoliation of the black spots and the resultant deterioration of corrosion resistance occasionally occur in the member having a structure in which stress is loaded on the weld zone. [00101 Therefore, in order to improve the corrosion resistance of the TIG weld zone, it is important to not only improve the corrosion resistance of the weld bead portion itself and weld scale portion itself, but also to control the occurrence of black spots in the weld zone. The scale that is generated during the welding and accompanies the change of color can be mostly suppressed by the method of enhancing shielding conditions during welding. However, the black spots generated in the TIG weld zone could not be suppressed sufficiently in accordance with the prior arts even when the shielding conditions were enhanced. [00111 In consideration of the above-explained circumstances, an object of the present invention is to provide a ferritic stainless steel that is resistant to the generation of black spots in the TIG weld zone and exhibits excellent corrosion resistance and workability in the weld zone. Solution to the Problems [00121 As described below, the inventors performed extensive research to suppress the amount of generation of black spots. As a result, the inventors found that the generation of black spots in the TIG weld zone could be suppressed by optimizing the amounts of Al, Ti, Si, and Ca, and reached the invention of the ferritic stainless steel in which black spots are generated only in a small amount. [00131 The followings are summary of the present invention. A first aspect of the present invention is a ferritic stainless steel containing, in mass %, 0.020 % or less of C, 0.025% or less of N, 1.0% or less of Si, 1.0% or less of Mn, 0.035% or less of P, 0.01% or less of S, 16.0 to 25.0% of Cr, 0.12% or less of Al, 0.05 to 0.35% of Ti, and 0.0015% or less of Ca, and the balance consisting of Fe and unavoidable impurities, wherein the following formula 1 is satisfied. BI = 3A1+ Ti + 0.5Si + 200Ca < 0.8 ....... 1, where Al, Ti, Si, and Ca in the formula 1 each denotes an amount of each element in mass % of the steel. In the above-described ferritic stainless steel, only a small amount of black spots is generated in the weld zone. [00141 A second aspect of the present invention is a ferritic stainless steel according to the above-described first aspect, and further contains, in mass %, 0.6% or less of Nb. A third aspect of the present invention is a ferritic stainless steel according to the above-described first or second aspect, and further contains, in mass %, 3.0% or less of Mo.

A fourth aspect of the present invention is a ferritic stainless steel according to any one of the above-described first to third aspects, and further contains, in mass %, one or two selected from 2.0% or less of Cu and 2.0% or less of Ni. A fifth aspect of the present invention is a ferritic stainless steel according to any one of the above-described first to fourth aspects, and further contains, in mass %, one or two selected from 0.2% or less of V and 0.2% or less of Zr. A sixth aspect of the present invention is a ferritic stainless steel according to any one of the above-described first to fifth aspects, and further contains, in mass %, 0.005% or less of B. Effect of the invention [00151 According to the present invention, it is possible to provide a ferritic stainless steel in which black spots do not easily occur and that is excellent in corrosion resistance and workability of the weld zone. BRIEF EXPLANATION OF DRAWINGS [00161 FIG. 1A is a photograph that shows appearance of black spots that were generated in the back side during TIG welding. FIG. 1B is a schematic drawing that corresponds to the photograph of FIG. 1A and shows an appearance of black spots that were generated in the back side during TIG welding. FIG. 2A is a graph that shows a result of AES measurement of depth profile of elements (concentration distributions of elements in the depth direction) of the weld bead portion in the back side of a test piece. FIG. 2B is a graph that shows a result of AES measurement of depth profile of elements (concentration distributions of elements in the depth direction) of a black spot in the back side of a test piece. FIG. 3 is a graph that shows a relationship between the BI value and the formation length ratio of black spots. FIG. 4 is a graph showing the relationship between the BI value and corrosion, where concentric double circles (@) show excellent results, circles (0 ) show good results, and crosses (x) show bad results. MODE FOR CARRYING OUT THE INVENTION [00171 In the following, the present invention is explained in detail. A ferritic stainless steel according to the present invention that generates only a small amount of black spot satisfies the below described formula 1. BI = 3A1+ Ti + 0.5Si + 20OCa <O0.8 ...1, where Al, Ti, Si, and Ca in the formula 1 each denotes an amount of each element in the steel in mass %. [00181 Al, Ti, Si, and Ca are elements that have a specifically strong affinity with oxygen and that generate black spots at the time of TIG welding. As the amount of Al, Ti, Si, and Ca contained in the steel increases, black spots are easily generated. The coefficients of the amounts of Al, Ti, Si, and Ca in the above-described formula 1 are determined based on the degree (strength) of the effect of enhancing the generation of black spots and the amounts in the steel. Specifically, as it is shown in the following experimental example, Al is an element that is included in the black spot at the highest concentration and has a specifically large effect of enhancing the generation of black spots. Therefore, coefficient of the Al content in the above-described formula 1 is determined to be 3. Ca is an element that is included in the black spot at a high concentration regardless of its small content in the steel and that has a large effect of enhancing the generation of black spots. Therefore, the coefficient of the Ca content is determined to be 200. [00191 Where the above-described BI value exceeds 0.8, the generation of black spots is prominent. On the other hand, where the BI value is 0.8 or less, the generation of black spots in the TIG weld zone is sufficiently reduced, and an excellent corrosion resistance is obtained. Where the BI value is 0.6 or less, it is possible to suppress the generation of black spots more effectively. Further, where the BI value is 0.4 or less, the generation of black spots is mostly suppressed, and it is possible to further improve the corrosion resistance of the TIG weld zone. [00201 Under conditions in which a large amount of black spots tend to occur, the black spot portion has a large thickness. It is considered that such a portion is easily exfoliated at the time of working, and that severe working such as bulging causes the exfoliation and provides a starting point for corrosion. On the contrary, the black spots have thin thickness under conditions in which black spots are generated in a small amount. Therefore, it is considered that even when black spots are generated, the black spots are not exfoliated easily. Therefore, it is considered that corrosion resistance of the weld zone can be suppressed by suppressing the generation of black spots. [00211 Next, component compositions of the ferritic stainless steel according to the present invention are explained in detail. Firstly, each of the elements for regulating the above described formula 1 is explained. Aluminum (Al): 0.012% by mass or less Al is important as an deoxidizing element and has an effect in grain-refinement of the microstructure of the steel by controlling the composition of non-metallic inclusion. However, Al is an element that has the largest contribution to the generation of black spots. In addition, excessive addition of Al causes coarsening of the non-metallic inclusions that may act as starting points of scratching in the product. Therefore, the upper limit of the amount of Al was determined to be 0.12%. It is preferable for the steel to contain 0.01% or more of Al with the purpose of deoxidization. More preferably, the amount of Al is 0.03% to 0.10%. [00221 Titanium (Ti): 0.05% to 0.35% by mass Ti is an very important element for fixing C and N and suppressing grain boundary corrosion in the weld zone, thereby improving workability. However, excessive addition of Ti results in not only generation of black spots but also occurrence of surface scratches during the production process. Therefore, the range of the amount of Ti was determined to be 0.05% to 0.35%. More preferable range is 0.07% to 0.20%. Silicon (Si): 1.0% by mass or less Si is an important element as an deoxidizing element and is effective in improvement of corrosion resistance and oxidation resistance. However, excessive addition of Si results in not only enhancement of generation of black spots but also deterioration of workability and productivity. Therefore, the upper limit of the amount of Si was determined to be 1.0%. It is preferable to make the steel contain 0.01% or more of Si for the purpose of deoxidization. Preferably, the amount of Si is 0.05% to 0.55%. [00231 Calcium (Ca): 0.0015% by mass or less Ca is very important as an deoxidizing element and is contained in the steel in small amount in the form of non-metallic inclusion. On the other hand, since Ca is oxidized very easily, Ca behaves as strong cause of generation of black spots in the time of welding. In addition, there is a case in that Ca causes generation of water-soluble inclusion, thereby deteriorating corrosion resistance. Therefore, it is preferable to control the amount of Ca to be as small as possible, and the upper limit of the amount of Ca was determined to be 0.0015%. More preferably, the amount of Ca is 0.0012% or less. [00241 Next, the other elements constituting the ferritic stainless steel according to the present invention is explained. Carbon (C): 0.020% or less by mass. The amount of C must be suppressed since C deteriorates grain boundary corrosion resistance and workability. Therefore the upper limit of C was determined to be 0.020%. On the other hand, excessive reduction of C causes an increase in the refining cost. Therefore, the amount of C is preferably 0.002% to 0.015%. Nitrogen (N): 0.025% or less by mass In the same manner as C, N deteriorates grain boundary corrosion resistance and the workability of the steel. Therefore, it is necessary to reduce the amount of N. Therefore, upper limit of the amount of N was determined to be 0.025%. On the other hand, excessive reduction of N causes an increase in the refining cost. Therefore, the amount of N is preferably 0.002% to 0.015%. [00251 Manganese (Mn): 1.0% or less by mass Although Mn is an important element as a deoxidizing element, excessive addition of Mn tends to cause generation of MnS that acts as a starting point of corrosion, and destabilizes the ferrite microstructure. Therefore, the amount of Mn was controlled to be 1.0% or less. For the purpose of deoxidization, it is preferable for the steel to contain 0.01% or more of Mn. Preferably, the amount of Mn is 0.05% to 0.5%, and more preferably, 0.05% to 0.3%. Phosphorous (P): 0.035% or less by mass The amount of P must be suppressed to low value since P deteriorates weldability and workability and makes the grain boundary corrosion easily occur. Therefore, the amount of P was controlled to be 0.035% or less. A more preferable amount of P is 0.001% to 0.02%. [00261 Sulfur (S): 0.01% or less by mass The amount of S must be reduced since S generates water-soluble inclusions such as CaS and MnS that act as starting points of corrosion. Therefore, the amount of S is controlled to be 0.01% or less. On the other hand, excessive reduction of S results in deterioration of the cost. Therefore, the amount of S is preferably 0.0001% to 0.005%. [00271 Chromium (Cr): 16.0% to 25.0% by mass Cr is the most important element for ensuring corrosion resistance of the stainless steel. In order to stabilize the ferrite microstructure, it is necessary for the steel to contain 16.0% or more of Cr. On the other hand Cr deteriorates the workability and productivity of the steel. Therefore, the upper limit of Cr content was determined to be 25.0%. Preferably, the amount of Cr is 16.5% to 23.0%, and more preferably, 18.0% to 22.5%. [00281 Niobium (Nb): 0.6% by mass or less Nb has properties such that Nb may be added alone, or in combination with Ti. Where Nb and Ti are added in combination, it is preferable that the formula: (Ti+Nb)/(C+N) 6 is satisfied, where Ti, Nb, C, and N in the formula each denote the amount in mass % of each element in the steel. In the same manner as Ti, Nb fixes C and N, suppress grain boundary corrosion of weld-zone, and improves workability. On the other hand, excessive addition of Nb deteriorates workability of the steel. Therefore, it is preferable to control the upper limit of the amount of Nb to be 0.6%. In order to improve the above-described properties by the content of Nb, it is preferable for the steel to contain 0.05% or more of Nb. Preferably, the amount of Nb is 0.15% to 0.55%. [00291 Molibdenum (Mo): 3.0% or less by mass Mo is an element that has an effect of repairing the passive film and is very effective in improvement of corrosion resistance. By being added in combination with Cr, Mo has an effect of improving pitting corrosion resistance of the steel. By being added in combination with Ni, Mo has an effect of improving the resistance to outflow rust. On the other hand, increased Mo reduces workability and increases the cost. Therefore, it is preferable to control the upper limit of the amount of Mo to be 3.0%. In order to improve the above-described properties by the content of Mo, it is preferable for the steel to contain 0.30% or more of Mo. Preferably, the amount of Mo is 0.60% to 2.5%, more preferably, 0.9% to 2.0%. [00301 Nickel (Ni): 2.0% or less by mass Ni has an effect of suppressing active dissolution rate, and is excellent in repassivation properties because of the small hydrogen overvoltage. On the other hand, excessive addition of Ni deteriorates workability and destabilizes the ferrite microstructure. Therefore, it is preferable to control the upper limit of the amount of Ni to be 2.0%. In order to improve the above-described properties by the content of Ni, it is preferable for the steel to contain 0.05% or more of Ni. Preferably, the amount of Ni is 0.1% to 1.2%, more preferably, 0.2% to 1.1%. [00311 Copper (Cu): 2.0% or less by mass In the same manner as Ni, Cu reduces the active dissolution rate, and has an effect of enhancing repassivation. However, an excessive addition of Cu deteriorates the workability. Therefore, where Cu is added, it is preferable to control the upper limit of the amount to be 2.0%. In order to improve the above-described property by the content of Cu, it is preferable for the steel to contain 0.05% or more of Cu. Preferably, the amount of Cu is 0.2% to 1.5%, more preferably, 0.25% to 1.1%. [00321 Vanadium (V) and/or zirconium (Zr): 0.2% by mass or less V and Zr improve weather resistance and crevice corrosion resistance. In addition, where V is added while suppressing the use of Cr and Mo, it is possible to ensure an excellent workability. On the other hand, excessive addition of V and/or Zr deteriorates workability, and saturates the effect of improving corrosion resistance. Therefore, where V and/or Zr is contained, it is preferable to control the upper limit of the amount to be 0.2%. In order to improve the above-described properties by the content of V and/or Zr, it is preferable for the steel to contain 0.03% or more of V and/or Zr. More preferably, the amount of V and/or Zr is 0.05% to 0.1%. [00331 Boron (B): 0.005% or less by mass B is an element that strengthens grain boundary and is effective in improvement of secondary working embrittlement. On the other hand, excessive addition of B causes reduction of ductility by solution-strengthening of ferrite. Therefore, where B is added, it is preferable to control the lower limit to be 0.0001%, and the upper limit to be 0.005%. More preferably, the amount of B is controlled to be 0.0002% to 0.0020%. EXAMPLE [00341 Test pieces composed of ferritic stainless steel each having a chemical component (composition) shown in Table 1 were produced in accordance with the below described method. Firstly, a cast steel having a chemical component (composition) shown in Table 1 was molten by vacuum melting, and an ingot having a thickness of 40 mm was produced from the melt. The ingot was rolled to a thickness of 5 mm by hot rolling. After that, in accordance with the recrystallization behavior of each steel, the rolled steel was heat treated for one minute at a temperature of 800 to 10OOoC. After removing a scale by grinding, steel plates having a thickness of 0.8 mm were produced by cold rolling. After removing the surface oxide scale by pickling (acid cleaning), test materials were obtained. Using the test materials, test pieces of Nos. 1 to 28 were produced. In the chemical component (composition) shown in Table 1, the amount of each element is shown in mass %, and the balance is iron and unavoidable impurities. The under-line shows that the value is outside the range of the present invention. [00351 Table 1 Fe and No. C Si Mn P S Cr Al Ti Ca N Mo Nb Ni Cu B V Zr unavoidable impurities 1 0.004 0.10 0.11 0.007 0.001 18.0 0.04 0.20 0.0002 0.008 Balance inventive 2 0.005 0.11 0.20 0.015 0.003 18.2 0.06 0.12 0.0002 0.007 0.52 Balance inventive 3 0.008 0.09 0.20 0.011 0.002 19.7 0.04 0.12 0.0003 0.012 0.20 Balance inventive 4 0.011 0.10 0.11 0.009 0.001 22.9 0.03 0.10 0.0003 0.010 0.31 0.05 Balance inventive 5 0.012 0.11 0.18 0.009 0.001 18.7 0.03 0.16 0.0004 0.011 1.81 0.28 Balance inventive 6 0.005 0.08 0.20 0.008 0.001 22.5 0.07 0.09 0.0002 0.008 1.18 0.18 Balance inventive 7 0.007 0.10 0.14 0.010 0.002 19.0 0.04 0.14 0.0004 0.010 0.99 0.22 Balance inventive 8 0.010 0.13 0.15 0.010 0.002 18.4 0.04 0.16 0.0002 0.010 1.90 0.23 0.12 0.20 0.10 Balance inventive 9 0.004 0.12 0.18 0.009 0.003 22.6 0.05 0.13 0.0003 0.011 0.82 0.25 0.15 0.15 0.08 Balance inventive 10 0.007 0.51 0.25 0.010 0.002 19.1 0.01 0.07 0.0002 0.009 0.45 0.28 0.44 Balance inventive 11 0.004 0.10 0.16 0.009 0.001 20.9 0.03 0.06 0.0002 0.009 0.25 0.0007 Balance inventive 12 0.007 0.12 0.25 0.010 0.002 19.1 0.06 0.12 0.0002 0.009 0.95 0.21 1.02 0.06 Balance inventive 13 0.014 0.04 0.22 0.020 0.003 17.5 0.04 0.08 0.0005 0.014 0.51 0.12 Balance inventive 14 0.003 0.45 0.27 0.011 0.002 19.4 0.05 0.09 0.0003 0.006 0.17 0.40 0.50 0.0004 0.12 Balance inventive 15 0.009 0.08 0.09 0.008 0.002 18.5 0.08 0.08 0.0004 0.008 0.55 Balance inventive 16 0.004 0.12 0.20 0.022 0.002 23.0 0.12 0.19 0.0002 0.008 0.55 Balance inventive 17 0.005 0.15 0.21 0.020 0.003 19.2 0.04 0.30 0.0009 0.009 0.25 0.39 Balance inventive 18 0.004 0.10 0.14 0.007 0.001 17.1 0.04 0.22 0.0003 0.009 Balance inventive 19 0.004 0.12 0.12 0.008 0.003 23.7 0.06 0.15 0.0005 0.011 1.85 0.21 Balance inventive 20 0.013 0.62 0.25 0.020 0.003 17.6 0.06 0.07 0.0004 0.014 0.38 Balance inventive 21 0.005 0.09 0.28 0.015 0.002 23.8 0.08 0.21 0.0010 0.010 0.19 0.0008 0.09 Balance inventive 22 0.010 0.25 0.20 0.030 0.003 23.0 0.15 0.19 0.0015 0.012 0.22 Balance comparative 23 0.006 0.65 0.21 0.015 0.002 18.5 0.05 0.02 0.0010 0.009 0.41 0.25 0.39 Balance comparative 24 0.004 0.20 0.22 0.020 0.003 21.5 0.09 0.34 0.0010 0.010 1.05 0.11 Balance comparative 25 0.006 0.26 0.16 0.025 0.001 15.9 0.09 0.21 0.0009 0.014 0.0010 Balance comparative 26 0.010 0.25 0.20 0.020 0.002 17.9 0.03 0.40 0.0015 0.011 2.01 Balance comparative 27 0.015 1.01 0.31 0.002 0.002 18.0 0.04 0.19 0.0014 0.014 0.36 Balance comparative 28 0.012 0.28 0.23 0.018 0.003 23.5 0.10 0.21 0.0019 0.012 1.56 0.18 0.08 Balance comparative [00361 The thus obtained test pieces of Nos. 1 to 28 were subjected to TIG welding under the following welding conditions, and formation length ratio of black spot was measured in accordance with the following manner. In addition, corrosion experiment was performed for the test piece of Nos. 1 to 28. Welding conditions Pieces of the same steel were butted and subjected to TIG welding with feed rate of 50 cm/min, and heat input of 550 to 650J/cm 2 . Argon was used both in shielding of torch side and shielding of back side. [00371 Ratio of formation length of black spot The formation length ratio of black spots was determined as a standard for showing the amount of generated black spots after the TIG welding. The formation length ratio of black spots was obtained by integrating length of each black spot along the welding direction, and dividing the integrated value by the total welding length. Practically, photograph of a 10 cm length weld zone was taken by a digital camera, length of each black spot was measured, and ratio of the integrated length of black spots to the welding length was calculated using image processing. [00381 Corrosion test TIG weld zones of test pieces were subjected to bulging and were used as test pieces for corrosion test. Erichsen test conditions in accordance with JIS2247 were used as the bulging conditions. The penetration side was used as the surface, and a punch of 20 mm 0 was used in the bulging. The working of each test piece was paused so as to adjust the working conditions with respect to the height of the bulge. The paused height (height of bulge) was standardized to 6 mm and 7 mm. Each test piece was subjected to continuous spray test of 5%NaCl in accordance with JIS Z 2371, and corrosion was evaluated by presence or absence of outflow rust in the test piece at 48 hours after the spray test. Where the outflow rust was not observed in the bulged test piece with bulging height of 6 mm after the continuous spray test of 5%NaCl, the result was evaluated as "GOOD". Where the outflow rust was not observed in the bulged test piece with bulging height of 7 mm after the same spray test, the result was evaluated as "EXCELLENT". Where the outflow rust occurred after the continuous spray test, the result was evaluated as BAD. BI values determined from the chemical component in Table 1, formation length ratio of black spots, and the results of corrosion test are shown in Table 2. [00391 Table 2 No. BI Formation length ratio Results of corrosion of black spots (%) test 1 0.40 10 EXCELLENT inventive 2 0.40 7 EXCELLENT inventive 3 0.35 3 EXCELLENT inventive 4 0.30 0 EXCELLENT inventive 5 0.39 9 EXCELLENT inventive 6 0.38 7 EXCELLENT inventive 7 0.39 9 EXCELLENT inventive 8 0.39 10 EXCELLENT inventive 9 0.40 8 EXCELLENT inventive 10 0.40 9 EXCELLENT inventive 11 0.24 0 EXCELLENT inventive 12 0.40 9 EXCELLENT inventive 13 0.32 7 EXCELLENT inventive 14 0.53 22 GOOD inventive 15 0.44 15 GOOD inventive 16 0.65 41 GOOD inventive 17 0.68 49 GOOD inventive 18 0.45 19 GOOD inventive 19 0.49 20 GOOD inventive 20 0.64 39 GOOD inventive 21 0.70 45 GOOD inventive 22 1.07 78 BAD comparative 23 0.70 45 BAD comparative 24 0.91 86 BAD comparative 25 0.79 60 BAD comparative 26 0.92 89 BAD comparative 27 1.10 83 BAD comparative 28 1.03 88 BAD comparative [00401 As shown in Table 2, formation length ratios of black spots were small, that is, amounts of generated black spots after the TIG welding were small in the test pieces Nos. 1 to 21 that had chemical component (composition) within the range of the present invention and BI value of 0.8 or less. Generation of black spots was suppressed in the test pieces No. 1 to 15, 18, and 19 having a BI value of 0.6 or less. Further, generation of black spots was mostly suppressed in Nos. 1 to 13 having a BI value of 0.4 or less such that the ratio of formation length of black spots was 10% or less. In test pieces No. 1 to 21 which were worked to have a bulge height of 6mm using an Erichsen test machine, rust from the weld zone was not observed after the continuous spray test of 5%NaCl. In test pieces No. 1 to 21 which were more severely worked to have a bulge height of 7mm, rust was not observed in test pieces having BI value of 0.4 or less, and rust was observed in test pieces having BI value exceeding 0.4. [00411 On the other hand, the test pieces Nos. 22, 24, 26 to 28 having BI value exceeding 0.8 showed large formation length ratio of black spots after the TIG welding and rust from the weld zone was observed in each specimen in the corrosion test. Magnified images of rust portions of test pieces Nos. 22, 24, 26 to 28 were observed using a magnifying glass. As a result, exfoliation was observed in the boundary between the black spots and the weld bead portion. Rust was generated in corrosion test of Nos. 22, 26, 27, and 28 in which concentrations of Al, Ti, Si, and Ca exceeded the regulated values. Occurrence of rust was observed in the corrosion test of the test piece No. 25 in which component ratio of Cr was less than 16% and the test piece No. 23 in which component ratio of Ti was less than 0.05%. [00421 Experimental example 1 Test materials were produced in accordance with the same manner as test piece No.1 except for that steel plates of 1 mm thick were produced by cold-rolling of ferritic stainless steels having the below described chemical components (compositions). Test piece A and test piece B were obtained using the test materials. Chemical component (composition) Test piece A C: 0.007%, N: 0.011%, Si: 0.12%, Mn: 0.18%, P: 0.22%, S: 0.001%, Cr: 19.4%, Al: 0.06%, Ti: 0.15%, Ca: 0.0005%, balance: iron and unavoidable impurities. Test piece B C: 0.009%, N: 0.010%, Si: 0.25%, Mn: 0.15%, P: 0.21%, S: 0.001%, Cr: 20.2%, Al: 0.15%, Ti: 0.19%, Ca: 0.0015%, balance: iron and unavoidable impurities. The thus obtained test piece A and test piece B were subjected to TIG welding under the similar welding conditions as the test piece No. 1, and appearance of black spots generated in the back side during TIG welding was observed. The results are shown in FIG. 1A and FIG. 1B. [00431 FIG. 1A is a photograph that shows an appearance of black spots generated in back side during TIG welding. FIG. 1B is a schematic drawing that shows an appearance of black spots generated in back side during TIG welding and that corresponds to FIG. 1A. In FIG. 1A and FIG. 1B, the left-side figures show a photograph and a drawing of test piece A in which BI value is 0.49, and the right-side figures show a photograph and a drawing of test piece B in which BI value is 1.07. As shown by the arrows in FIG. 1A and FIG. 1B, spot-like black spots are observed dispersingly both in the test piece A with BI value of 0.49 and test piece B with BI value of 1.07. However, it is recognized that the black spots are generated in larger amount in test piece B (right-side photograph) having a larger BI value. [00441 Two portions selected from the weld bead portion and the black spot portion of the test piece B with a BI value of 1.07 were subjected to auger electron spectroscopy (AES). The results are shown in FIG. 2A and FIG. 2B. A FE (Field Emission) Auger Electron Spectroscopy was used in the AES analysis, and the analysis was performed until intensity of oxygen spectrum was almost not detected under conditions of an acceleration voltage of 10keV, a spot diameter of 40 nm, and a sputtering rate of 15 nm/min. Although a position dependent error may occur due to small spot of AES measurement, the results were applied as values showing approximate thickness. [00451 FIG. 2A and FIG. 2B are graphs that show depth profile of elements (concentration distribution of elements in depth direction) in the black spot and the weld bead portion on the back side of the test piece as a result of AES analysis. FIG. 2A is a result of weld bead portion, and FIG. 2B is a result of a black spot. As shown in FIG. 2A, the weld bead portion was an oxide having a thickness of several hundred A that mainly contained Ti, and also contained Al and Si. On the other hand, as shown in FIG. 2B, the black spot was a thick oxide having a thickness of several thousandA that mainly contained Al, and also contained Ti, Si, and Ca. From the graph of black spot shown in FIG. 2B, it was confirmed that Al was contained in the black spot at the highest concentration and Ca was contained in the black spot at high concentration irrespective of its small amount in the steel. [00461 Experimental example 2 Test materials of ferritic stainless steel having various component ratios (compositions) were produced in accordance with the production method similar to that of test piece A, where each steel had a basic composition of C: 0.002 to 0.015%, N: 0.02 to 0.015%, Cr: 16.5 to 23%, Ni: 0 to 1.5%, Mo: 0 to 2.5%, and also contained main components of black spots such as Al, Ti, Si, and Ca in different amount. Using the test materials, a plurality of test pieces was obtained. The thus obtained plurality of test pieces were subjected to TIG welding under similar welding conditions as the test piece No. 1, and ratios of formation length of black spots were calculated in accordance with the same manner as the test piece No. 1. [00471 As a result, the formation length ratio of black spots tended to increase in accordance with the increasing amounts of Al, Ti, Si, and Ca. Those elements are elements having specifically strong affinity with oxygen. It was found that Al had the highest effect, and Ca had a strong influence on black spots irrespective of its small amount in the steel. It was also confirmed that Ti and Si also contributed to the generation of black spots. [00481 Based on the results, it was found that there was a strong possibility of generation of black spots even under shielding conditions where large amounts of Al, Ti, Si, and Ca were added, and that Al and Ti had strong influence on generation of black spots. [00491 BI value shown by the below described formula 1 was calculated for the plurality of test pieces, and the relationship between the BI value and the ratio of formation length of black spots was examined. BI = 3A1+ Ti + 0.5Si + 200Ca < 0.8 ....... 1, where Al, Ti, Si, and Ca in the formula 1 respectively denotes an amount of each element in mass % of the steel.

The results are shown in FIG. 3. FIG. 3 is a graph showing the relationship between the BI value and the ratio of formation length of black spots. As shown in FIG. 3, it is recognized that the ratio of formation length of black spots increases with an increasing BI value. [00501 Each of the plurality of test pieces was subjected to corrosion test in accordance with the same manner as the test piece No. 1. The results are shown in FIG. 4. FIG. 4 is a graph that shows a relationship between the BI values and the results of corrosion resistance evaluation after the spray test after working. In the figure, double circles (@) show excellent results, circles ( 0) show good results, and crosses (x) show bad results. As shown in FIG. 4, corrosion did not occur in the specimen with bulge height of 6 mm where BI value was 0.8 or less. Especially, where BI value was 0.4 or less, specifically good results were achieved such that corrosion was not observed in the specimen with bulge height of 7 mm. INDUSTRIAL APPLICABILITY [00511 The ferritic stainless steel of the present invention can be appropriately used in members requiring corrosion resistance in a structure of, for example, exterior materials, building materials, water or hot water containers, consumer electronics, kitchen equipment, drain water collectors and heat exchanger of gas condensing boiler, various welded pipes or the like that are formed by TIG welding and used in general indoor or outdoor environment. Specifically, the ferritic stainless steel of the present invention is appropriately used in a member that is subjected to working after the welding. Since the ferritic stainless steel of the present invention is excellent not only in corrosion resistance but also in workability of TIG weld zone, the steel can be widely used in the usage suffering severe working conditions.

Claims

1. A ferritic stainless steel containing, in mass %, 0.020 % or less of C, 0.025% or less of N, 1.0% or less of Si, 1.0% or less of Mn, 0.035% or less of P, 0.01% or less of S, 16.0 to 25.0% of Cr, 0.12% or less of Al, 0.05 to 0.35% of Ti, and 0.0015% or less of Ca, and the balance consisting of Fe and unavoidable impurities, wherein the following formula 1 is satisfied. BI = 3A1+ Ti + 0.5Si + 20OCa <0.8 ....... 1, where Al, Ti, Si, and Ca in the formula 1 each denotes an amount of each element in mass % of the steel.

2. A ferritic stainless steel according to claim 1, further containing, in mass %, 0.6% or less of Nb.

3. A ferritic stainless steel according to claim 1, further containing, in mass %, 3.0% or less of Mo.

4. A ferritic stainless steel according to claim 2, further containing, in mass %, 3.0% or less of Mo.

5. A ferritic stainless steel according to any one of claims 1 to 4, further containing, in mass %, one or two selected from 2.0% or less of Cu and 2.0% or less of Ni.

6. A ferritic stainless steel according to any one of claims 1 to 4, further containing, in mass %, one or two selected from 0.2% or less of V and 0.2% or less of Zr.

7. A ferritic stainless steel according to claim 5, further containing, in mass %, one or two selected from 0.2% or less of V and 0.2% or less of Zr.

8. A ferritic stainless steel according to any one of claims 1 to 4, further containing, in mass %, 0.005% or less of B.

9. A ferritic stainless steel according to claim 5, further containing, in mass %, 0.005% or less of B.

10. A ferritic stainless steel according to claim 6, further containing, in mass %, 0.005% or less of B.

11. A ferritic stainless steel according to claim 7, further containing, in mass %, 0.005% or less of B.