Formable thin steel sheets and method of producing the same

Abstract: A formable thin steel sheet such as hot rolled sheet, cold rolled sheet or surface treated sheet comprises not more than 0.003 wt% of C, not more than 1.0 wt% of Si, not more than 1.0 wt% of Mn, not more than 0.15 wt% of P, not more than 0.020 wt% of S, not more than 0.0045 wt% of O, not more than 0.0020 wt% of N, not more than 0.15 wt% of Al provided that a ratio of Al/N is not less than 30, and the balance being Fe and inevitable impurities, and has not only improved formability for press forming, deep drawing or the like but also improved fatigue resistance as a welded joint.

Description: This invention relates to hot rolled steel sheets, cold rolled steel sheets and surface treated steel sheets having not only improved formability for press forming, deep drawing or the like but also improved fatigue resistance at welded joints. In general, the thin steel sheets are widely used for press forming, deep drawing and the like. However, the thin steel sheets are also required to have properties which depend on their intended use. For example, the thin steel sheets are frequently subjected to welding, particularly, spot welding whether or not they are cold rolled sheets, hot rolled sheets or surface treated sheets. In particular, thin steel sheet is used for automobiles. In this case, the number of spot welds per vehicle amounts to several thousand and stress concentration may result in the welded joint when a load is applied from exterior. That is, fatigue breakage due to repeated stress concentration in the welded joints during running of the vehicle results in the occurrence of serious accidents. In the formable thin steel sheet, therefore, the fatigue resistance of the welded joint is a very important characteristic. Extreme-low carbon steels having a formability higher than that of the conventional low carbon steel are frequently used for the thin steel sheet. However, the fatigue strength of extreme-low carbon steel may be lowered due to poor texture of heat-affected zone in the welded joint as a result of the welding conditions. Moreover, improvements in the safety of machines and structures such as automobiles and the like are universally sought, and consequently it is important to enhance the fatigue strength of the welded joint above that obtained when using conventional steel sheets. In this connection, various steel sheets have been proposed in Japanese Patent laid open No. 54-135616, No. 53-52222, No. 61-246344, No. 58-25436, No. 53-137021, No. 58-110659 and the like. However, all of these techniques disclose the mechanical properties of the cold rolled steel sheet but are silent about the fatigue strength of the welded joint. Furthermore, Japanese Patent laid open No. 63-317625 discloses a method of restricting amounts of Ti, Nb and B to particular ranges to improve the fatigue resistance of the welded joint in the steel sheet. In this method, however, the tensile shear fatigue properties in the spot welded zone are considered, but there is no consideration of the cross tensile fatigue properties. Moreover, Japanese Patent laid open No. 225748 discloses cold rolled steel sheets having excellent fatigue properties, but in this case the fatigue properties of the sheet itself are merely improved. It is, therefore, an object of the invention to provide thin steel sheets having not only an improved formability for press forming, deep drawing or the like but also excellent fatigue resistance at welded joints, particularly fatigue resistance in spot welding. According to a first aspect of the invention there is provided a formable steel sheet exhibiting fatigue resistance at welded joints, the steel comprising; C in an amount of not more than 0.003% by weight, Si in an amount of not more than 1.0% by weight, Mn in an amount of not more than 1.0% by weight, P in an amount of not more than 0.15% by weight, S in an amount of not less than 0.0035 to not more than 0.020% by weight, O in an amount of not more than 0.0045% by weight, N in an amount of not more than 0.0020% by weight, Al in an amount of not more than 0.15% by weight, provided that the ratio Al/N is not less than 30, the steel optionally including at least one of: Nb in an amount of not less than 0.001 to not more than 0.025% by weight, B in an amount of not less than 0.0002 to not more than 0.002% by weight, Ti in an amount of not more than 0.10% by weight, V in an amount of not more than 0.10% by weight, Zr in an amount of not more than 0.10% by weight, Ca in an amount of not more than 0.10% by weight, Cr in an amount of not more than 1.0% by weight, Cu in an amount of not more than 1.0% by weight, and Ni in an amount of not more than 1.0% by weight, the balance being iron and incidental impurities. In a preferred embodiment the steel sheet contains at least one of 0.001-0.025 wt% of Nb and 0.0002-0.0020 wt% of B, or further contains at least one of not more than 0.10 wt% of Ti, not more than 0.10 wt% of V, not more than 0.10 wt% of Zr, not more than 0.10 wt% of Ca, not more than 1.0 wt% of Cr, not more than 1.0 wt% of Cu and not more than 1.0 wt% of Ni. According to a second aspect of the invention there is provided a method of producing formable steel sheet having improved fatigue resistance at welded joints, the method comprising the steps: (a) hot rolling the steel sheet of claim 1 at a finish temperature of not less than 600°C, (b) cold rolling the hot rolled steel sheet at a rolling reduction of not less than 60%, and (c) subjecting the cold rolled steel sheet to recrystallization annealing at a temperature of not more than the A C3 transformation point. In preferred embodiments the hot rolled sheet is coiled at a coiling temperature of not lower than 200°C after the hot rolling, and the resulting thin steel sheet is subjected to a galvanising or electroplating. For a better understanding of the invention and to show how the same may be carried into effect, reference will now be made by way of example only to the accompanying drawings in which: Fig. 1 is a graph showing the relationship between the oxygen amount, the Al/N ratio and the value of the tensile shear fatigue limit in the spot welded joint of the cold rolled steel sheet; Fig. 2 is a graph showing the relationship between the oxygen amount, the Al/N ratio and the value of the tensile shear fatigue limit in the spot welded joint of the hot rolled steel sheet; Fig. 3 is a graph showing the relationship between the oxygen amount and the value of the tensile shear fatigue limit in the spot welded joint when the Al/N ratio of the hot rolled steel sheet is about 37; Fig. 4 is a schematic sectional view of a specimen used for the tensile shear fatigue test of a spot welded joint, showing the position of a crack produced in the fatigue test; Fig. 5 is a graph showing the relationship between the oxygen amount, the Al/N ratio and the value of the cross tensile fatigue limit in the spot welded joint; Figs. 6a and 6b are graphs showing the relationship between the Al/N ratio and the value of the cross tensile fatigue limit and the tensile shear fatigue limit in the spot welded joint when oxygen amount is about 0.0030 wt%; and Figs. 7a and 7b are schematic views showing modes of a spot welded specimen in the tensile shear fatigue test and the cross tensile fatigue test, respectively. The inventors have made various studies with respect to the influence of steel components on the fatigue properties of the welded joint, particularly fatigue properties of the spot welded joint, and discovered the following facts which are described below. The invention is described with respect to experimental results leading to success of the invention. The fatigue test employed for the spot welded joint is carried out by a fatigue test method for spot welded joints according to JIS Z3138. The fatigue limit value means the upper limit of loading range when loading is applied to the test specimen 10,000,000 times. Fig. 1 shows the relationship between the oxygen amount, the Al/N ratio and the tensile shear fatigue limit value at the spot welded joint in a cold rolled steel sheet of 0.8 mm in thickness. The chemical composition of steels used in the fatigue test is shown in Table 1, and the conditions of the spot welding are shown in Table 2. The steel sheet was hot rolled at a finish temperature of about 900°C, cold rolled at a rolling reduction of 75-80% and continuously annealed at a temperature of 820-840°C. In Fig. 1, the shadowed area shows a region in which the fatigue limit value is higher by 10% or more than that of the conventional low carbon aluminum killed and box annealed steel sheet (tensile shear fatigue limit: 82 kgf (804 N)). This corresponds to a region in which the oxygen amount is not more than 0.0045 wt% and the Al/N ratio is not less than 30. Sample size Welding conditions Average nugget diameter (mm) width (mm) length (mm) chip welding force welding current 40 150 Cr-Cu, 4.8 mm, CF model 200 kgf (196 N) 8.5∼9.5 kA 5.0 Fig. 2 shows the relationship between the oxygen amount, the Al/N ratio and the tensile shear fatigue limit value of a spot welded joint of a hot rolled steel sheet of 2.6 mm in thickness. The chemical composition of steels used in the fatigue test is shown in Table 3, and the conditions of the spot welding are shown in Table 4. The steel sheet was hot rolled at a finish temperature of about 900°C and coiled at a coiling temperature of 550°C. In Fig. 2, the shadowed area shows a region in which the fatigue limit value is higher by 10% or more than that of the conventional low carbon aluminum killed and hot rolled steel sheet (tensile shear fatigue limit: 168 kgf (1648 N)). This corresponds to a region in which the oxygen amount is not more than 0.0045 wt% and the Al/N ratio is not less than 30, as for the case of the cold rolled sheet. Sample size Welding conditions Average nugget diameter (mm) width (mm) length (mm) chip welding force welding current 50 180 Cr-Cu, 9 mm, CF model 650 kgf (6376 N) 12∼14 kA 10.0 Fig. 3 shows the relationship between the tensile shear fatigue limit value and the oxygen amount when the Al/N ratio is about 37. It is clear that a fatigue limit value higher than the conventional low carbon aluminum killed and hot rolled steel sheet (tensile shear fatigue limit: 168 kgf (1648 N)) is obtained when the O amount is not more than 0.0045 wt%. In these tests, the breakage due to fatigue results from the occurrence of cracks generated at the heat-affected zone as shown in Fig. 4, in which letter A is the position of a crack generated, letter B a nugget portion, letter C a heat-affected zone and letter D a thin steel sheet. In order to understand these observations, the inventors have investigated the hardness distribution in a section of a welded zone of a specimen having a high fatigue limit value. The inventors found that the hardness difference ranging from the fused zone to the heat-affected zone is small compared with a steel sheet having a low fatigue limit value, and is smooth in its distribution. From this fact, it is considered that such a small hardness difference effectively acts to reduce the occurrence of fatigue cracks and the propagation thereof, which are due to stress concentration in the welded joint portion under stress loading. Furthermore, it can be seen from Figs. 1-3 that the fatigue limit value increases in steel sheets containing at least one of Nb and B within a defined amount. Alternatively, a cold rolled Ti-containing steel sheet of 0.7 mm thickness and having a chemical composition as shown in Table 5 was welded under spot welding conditions as shown in Table 6, and then subjected to a cross tensile fatigue test. In this case, the steel sheet was hot rolled at a finish temperature of about 900°C, cold rolled at a rolling reduction of 75-80% and continuously annealed at a temperature of 820-840°C. Sample size Welding conditions Average nugget diameter (mm) width (mm) length (mm) chip welding force welding current 50 150 Cr-Cu, 4.5 mm, CF model 165 kgf (1619 N) 7.2∼7.9 kA 4.0 In this test, the relationship between the oxygen amount, the Al/N ratio and the cross tensile fatigue limit value is shown in Fig. 5. From Fig. 5, it can be seen that the cross tensile fatigue limit value becomes considerably high when the oxygen amount and the Al/N ratio in both Ti-containing steel and Ti, Nb and B containing steel are within ranges shown by the shadowed region, that is, the oxygen amount is not more than 0.0045 wt% and the Al/N ratio is not less than 30. Fig. 6a shows the relationship between the cross tensile fatigue limit and the Al/N ratio when the oxygen amount is 0.0030 wt%. As seen from Fig. 6a, in both the Ti-containing steel and the Ti-Nb-B containing steel, a high fatigue limit value is obtained when the Al/N ratio is not less than 30. Furthermore, it is understood from the simultaneously conducted tensile shear fatigue test that the addition of Ti or Ti-Nb-B does not affect the fatigue limit as shown in Fig. 6b. Moreover, similar results are obtained for hot rolled steel sheets. The reason why an excellent cross tensile fatigue limit value is obtained under the above conditions is considered as follows: the breakage due to fatigue is led from the cracks generated at the heat-affected zone even in the cross tensile fatigue test. In case of Ti-containing steel, it is considered that the solid soluted Ti or Ti series precipitate acts to improve the toughness of the heat-affected zone, whereby the cross tensile fatigue properties are improved. It has also been found that a similar effect is obtained by adding at least one of Ti, V, Zr, Ca, Cr, Cu and Ni within defined ranges, in addition to the steel containing only Ti. For reference, the methods of the tensile shear and the cross tensile fatigue tests using spot welded specimens are schematically shown in Figs. 7a and 7b, respectively. As can be seen from Figs. 7a and 7b, the deformation mode is quite different between both the test methods. The reason why the chemical composition of the steel used in the invention is limited to the above range will be described below: C: The C amount should be considerably lower than that of conventional low carbon steel in order to obtain steels having a good elongation and r-value. Furthermore, the fatigue resistance improves as the C amount is reduced in the steel according to the invention. Therefore, the C amount is not more than 0.003 wt%, preferably not more than 0.0015 wt%. Si: The Si amount should be not more than 1.0 wt% because when the amount exceeds 1.0 wt%, the elongation and drawability of the steel sheet are degraded. Mn: The excessive addition of Mn degrades the elongation and drawability of the steel sheet, as for Si, so that the Mn amount should be not more than 1.0 wt%. P: When the P amount exceeds 0.15 wt%, P segregates into the grain boundary causing brittleness, hence it should be not more than 0.15 wt%. S: When the S amount is too small, the descaling property is degraded, making the surface properties bad, hence the lower limit is 0.0035 wt%. However, when the amount exceeds 0.020 wt%, the corrosion resistance is considerably degraded, so the upper limit is 0.020 wt%. O: The O amount is particularly important in the invention because it is considered that O in solid soluted state or in the form of oxide affects the occurrence and propagation of cracks. Therefore, in order to obtain fatigue properties higher than those of conventional low carbon steel sheet, the O amount must not be more than 0.0045 wt%. Preferably, it is not more than 0.0035 wt%. N: As the N amount becomes larger, the Al amount required becomes excessive, causing degradation of the surface properties as mentioned later. Therefore, the N amount is not more than 0.0020 wt%, preferably not more than 0.0017 wt%. Al: The Al amount is also important in the invention because it is considered that the fatigue properties are improved as a result of the influence of the distribution state of solid soluted Al or AlN precipitate upon the structure of the heat-affected zone. Therefore, it is closely related to the N amount. In order to improve the fatigue properties of the welded joint, it is required to have the Al (wt%)/N (wt%) ratio of not less than 30. However, when the Al amount is too large, the surface properties are degraded, so that the upper limit is 0.15 wt%. Nb, B: These elements are effective for the improving the fatigue properties, but when the amount added becomes excessive, the recrystallization temperature undesirably rises. Therefore, at least one of Nb and B may be added within ranges of 0.001 wt% ≦ Nb ≦ 0.025 wt% and 0.0002 wt% ≦ B ≦ 0.0020 wt%, respectively, for improving the fatigue properties. Ti, V, Zr, Ca, Cr, Cu, Ni: It is considered that each of these elements affects the structure of the heat-affected zone in a solid solution state or a precipitate state to enhance the fatigue properties. However, excessive addition degrades the quality of the steel sheet. Therefore, at least one of Ti, V, Zr, Ca, Cr, Cu and Ni may be added within ranges of not more than 0.10 wt% in each of Ti, V, Zr and Ca and not more than 1.0 wt% in each of Cr, Cu and Ni, respectively, for particularly improving the cross tensile fatigue properties. The invention will be described below with respect to preferable conditions in the production of formable thin steel sheets using steel of the above chemical composition as a starting material. In the production of hot rolled steel sheets, the finish temperature is limited to not lower than 600°C because when the finish temperature in the hot rolling is lower than 600°C, the deep drawability is degraded. The coiling temperature is limited to not lower than 200°C because when the coiling temperature is lower than 200°C, the quality is degraded. In the production of cold rolled steel sheets, the finish temperature of the hot rolling step is not lower than 600°C, preferably not lower than 800°C because when it is lower than 600°C, the deep drawability is degraded. The rolling reduction at the cold rolling step is not less than 60%, in order to obtain a satisfactory formability. The annealing temperature of the continuous annealing step after the cold rolling is not higher than A C3 point because when it is higher than A C3 point the crystal grains become coarse. The lower limit of the annealing temperature is not critical, but it is preferably higher by 30°C than the recrystallization temperature. As the annealing method, a box annealing may be used. Of course, these thin steel sheets may be subjected to a skin pass rolling within a usual range, i.e. about few percent of the sheet gauge (mm) for correcting the sheet shape and the like. Even if the thin steel sheet is subjected to a galvanizing or an electroplating, the breakage in the fatigue test is generated from the heat-affected zone, so that according to the invention, the thin steel sheet may be subsequently subjected to a surface treatment such as galvanizing, electroplating or the like. With regard to the welding method, the fatigue strength in the heat-affected zone is a problem whether or not the MIG method, the TIG method and the like are used in addition to the spot welding, so that the invention is effective for improving the fatigue strength of welded joint even in these welding methods. The following examples are given in illustration of the invention and are not intended as limitations thereof. Example 1 A steel having a chemical composition as shown in Table 7 was melted to form a slab, which was hot rolled at a finish temperature of 850-900°C, cold rolled at a rolling reduction of 71-78% and continuously annealed at an annealing temperature of 790-830°C to obtain a cold rolled steel sheet of 0.8 mm in thickness. Steel No. 18 was a conventional low carbon aluminum killed steel and was produced by box annealing. Steel Nos. 1-9 were acceptable in the invention, among which steel Nos. 1 and 8 were subjected to a galvanizing and electroplating, respectively. Steel Nos. 10-17 were comparative examples, whose chemical compositions were outside the range of the invention. The mechanical properties and tensile shear fatigue limit value at a spot welded joint (upper limit of loading range when the tensile loading was repeated 10,000,000 times) were measured with respect to these cold rolled steel sheets to obtain results as shown in Table 8. Moreover, a specimen of JIS Z2201 No. 5 was used in the tensile test, and the spot welding conditions and tensile shear fatigue test conditions were the same as in Table 2. As seen from Table 8, all of the steels according to the invention exhibit good mechanical properties and tensile shear fatigue limit values, while the comparative steels and the conventional steel are poor in either the mechanical properties or the tensile shear fatigue limit values. Furthermore, the surface treated steels according to the invention are naturally excellent in the properties as compared with the comparative and conventional steels because the breakage in the fatigue test is generated from the heat-affected zone. Moreover, in steel Nos. 5-9 containing either Nb or B or both, the fatigue resistance at the heat-affected zone is further improved, so that they exhibit higher tensile shear fatigue limit values than other steels according to the invention. Example 2 A steel having a chemical composition as shown in Table 9 was melted to form a slab, which was hot rolled at a finish temperature of 830-900°C and wound at a coiling temperature of 550-650°C to obtain a hot rolled steel sheet of 2.6 mm in thickness. Steel Nos. 1-9 were acceptable in the invention, among which steel Nos. 2 and 8 were subjected to a galvanizing and electroplating, respectively. Steel Nos. 10-17 were comparative examples, whose chemical compositions were outside the range of the invention, and steel No. 18 was a conventional low carbon aluminum killed steel. The mechanical properties and tensile shear fatigue limit value at spot welded joint portion (upper limit of loading range when the tensile loading was repeated 10,000,000 times) were measured with respect to these hot rolled steel sheets to obtain results as shown in Table 10. Moreover, a specimen of JIS Z2201 No. 5 was used in the tensile test, and the spot welding conditions and tensile shear fatigue test conditions were the same as in Table 4. As seen from Table 10, all of the steels according to the invention exhibit good mechanical properties and tensile shear fatigue limit values while the comparative steels and the conventional steel are poor in either the mechanical properties or the tensile shear fatigue limit values. Furthermore, the surface treated steels according to the invention are naturally excellent in the properties as compared with the comparative and conventional steels because the breakage in the fatigue test is generated from the heat-affected zone. Moreover, in steel Nos. 5-9 containing either Nb or B or both, the fatigue resistance at the heat-affected zone is further improved, so that they exhibit higher tensile shear fatigue limit values than other steels according to the invention. Example 3 A steel having a chemical composition as shown in Table 11 was melted to form a slab, which was subjected to the following treatments under production conditions as shown in Table 12. The hot rolled steel sheet of 2.6 mm in thickness was produced by subjecting the slab at a finish temperature of 830-900°C to winding at a coiling temperature of 550-650°C. Alternatively, the slab was hot rolled at a finish temperature of 830-920°C and coiled at a coiling temperature of 550-650°C to obtain a hot rolled sheet of 3.2 mm in thickness. Then the hot rolled sheet was cold rolled to a thickness of 0.7 mm at a rolling reduction of 78%, annealed at 750-880°C and further subjected to a skin pass rolling at 0.7%. Furthermore, a part of the hot rolled steel sheets and cold rolled steel sheets was subjected to galvanizing or electroplating. Steel Nos. 1-14 and Nos. 26-36 were acceptable in the invention, and steel Nos. 15-24 and Nos. 37-43 were comparative examples, whose chemical compositions were outside the range of the invention. Steel Nos. 25 and 44 were conventional low carbon aluminum killed steels, and steel No. 25 was produced by box annealing. The mechanical properties and cross tensile fatigue limit values at spot welded joint portion (upper limit of loading range when the tensile loading was repeated 10,000,000 times) were measured with respect to these thin steel sheets to obtain results as shown in Table 12. Moreover, a specimen of JIS Z2201 No. 5 was used in the tensile test, and the spot welding conditions and cross tensile fatigue test conditions were the same as in Table 6 in case of the cold rolled steel sheets and were carried out under conditions as shown in Table 13 in case of the hot rolled steel sheets. Sample size Welding conditions Average nugget diameter (mm) width (mm) length (mm) chip welding force welding current 50 150 Cr-Cu, 8.5 mm, CF model 650 kgf (6376 N) 14∼17 kA 7.8 As seen from Table 12, all of the steels according to the invention exhibit good mechanical properties and cross tensile fatigue limit values, while the comparative steels and the conventional steel are poor in either the mechanical properties or the cross tensile fatigue limit values. Furthermore, the surface treated steels according to the invention are excellent in the properties as compared with the comparative and conventional steels because the breakage in the fatigue test is generated from the heat-affected zone. Moreover, in steel Nos. 10-14 and Nos. 34-36 containing either Nb or B or both, the fatigue resistance at the heat-affected zone is further improved, so that they exhibit a higher cross tensile fatigue limit values than other steels according to the invention. As mentioned above, according to the invention, formable thin steel sheets having not only good formability for press forming, deep drawing or the like but also improved fatigue properties at welded joint are obtained, so that when they are applied to automobiles, structural members and the like, an increase in life or an improvement in safety is achieved.

Claims: A formable steel sheet exhibiting fatigue resistance at welded joints, the steel comprising; C in an amount of not more than 0.003% by weight, Si in an amount of not more than 1.0% by weight, Mn in an amount of not more than 1.0% by weight, P in an amount of not more than 0.15% by weight, S in an amount of not less than 0.0035 to not more than 0.020% by weight, O in an amount of not more than 0.0045% by weight, N in an amount of not more than 0.0020% by weight, Al in an amount of not more than 0.15% by weight, provided that the ratio Al/N is not less than 30, the steel optionally including at least one of: Nb in an amount of not less than 0.001 to not more than 0.025% by weight, B in an amount of not less than 0.0002 to not more than 0.002% by weight, Ti in an amount of not more than 0.10% by weight, V in an amount of not more than 0.10% by weight, Zr in an amount of not more than 0.10% by weight, Ca in an amount of not more than 0.10% by weight, Cr in an amount of not more than 1.0% by weight, Cu in an amount of not more than 1.0% by weight, and Ni in an amount of not more than 1.0% by weight, the balance being iron and incidental impurities. A method of producing formable steel sheet having improved fatigue resistance at welded joints, the method comprising the steps: (a) hot rolling the steel sheet of claim 1 at a finish temperature of not less than 600°C, (b) cold rolling the hot rolled steel sheet at a rolling reduction of not less than 60%, and (c) subjecting the cold rolled steel sheet to recrystallization annealing at a temperature of not more than the A C3 transformation point. A method as claimed in claim 2 wherein the hot rolled sheet is coiled at a coiling temperature of not less than 200°C after the hot rolling. A method as claimed in claim 3 wherein the steel sheet is galvanised or annealed after coiling.

Inventors: ABE HIDEO TECHNICAL RESEARCH D, KATO TOSHIYUKI TECHNICAL RESEA, NISHIMURA KEIJI CHIBA WORKS, OKADA SUSUMU TECHNICAL RESEARC, SATOH SUSUMU TECHNICAL RESEARC, YAMAZAKI YOSHIO TECHNICAL RESE, ABE, HIDEO TECHNICAL RESEARCH DIVISION, KATO, TOSHIYUKI TECHNICAL RESEARCH DIVISION, NISHIMURA, KEIJI CHIBA WORKS, OKADA, SUSUMU TECHNICAL RESEARCH DIVISION, SATOH, SUSUMU TECHNICAL RESEARCH DIVISION, YAMAZAKI, YOSHIO TECHNICAL RESEARCH DIVISION
Applicants: KAWASAKI STEEL CO, KAWASAKI STEEL CORPORATION
Application year: 1989
Main classification: C21D8
IPC codes: C21D8, C22C38