CA2403830C - High-workability steel pipe and method of producing same - Google Patents
High-workability steel pipe and method of producing same Download PDFInfo
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- CA2403830C CA2403830C CA002403830A CA2403830A CA2403830C CA 2403830 C CA2403830 C CA 2403830C CA 002403830 A CA002403830 A CA 002403830A CA 2403830 A CA2403830 A CA 2403830A CA 2403830 C CA2403830 C CA 2403830C
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- steel pipe
- steel
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- seam
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
- B21C37/08—Making tubes with welded or soldered seams
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B17/00—Tube-rolling by rollers of which the axes are arranged essentially perpendicular to the axis of the work, e.g. "axial" tube-rolling
- B21B17/14—Tube-rolling by rollers of which the axes are arranged essentially perpendicular to the axis of the work, e.g. "axial" tube-rolling without mandrel, e.g. stretch-reducing mills
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
Abstract
The invention provides a steel pipe being superior in workability, particularly in bending workability, in which an r-value in the axial direction of the pipe in a portion where melting or transformation of a steel material has occurred during seam welding is as high as comparable to that in a portion where melting or transformation of the steel material has not occurred, and a method of producing the steel pipe. In the high--workability steel pipe, an r-value in the longitudinal direction is not less than 1.2, more preferably not less than 1.6, over an entire area in the circumferential direction, including a seamed portion. The steel pipe is produced by a method comprising the step of performing diameter-reducing rolling on a steel pipe in a temperature range of from 600.degree.C to Ac3 with a reduction in diameter of not less than 30%, preferably after heating the steel pipe to temperatures of not lower than Ac1, the steel pipe being produced by seam--welding strip steel, or a method further comprising the step of performing heat treatment of holding the rolled steel pipe in a temperature range of from 600.degree.C to 900.degree.C for a time of 1 second or longer during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after the cooling.
Description
DESCRIPTION
HIGH-WORKABILITY STEEL PIPE AND METHOD OF PRODUCING
SAME
Technical Field The present invention relates to a steel pipe having superior workability and a method of producing the steel pipe.
Background Art For the purpose of reducing the weight and cost, the application of seam (electric resistance) welded steel pipes to automobile parts has been considered.
Conventional seam welded stee.l pipes, however, have not been sufficient in workability. Bending is employed to manufacture, e.g., undercarriage or suspension parts of automobiles. When the conventional seam welded steel pipes are subjected to the bending, a problem has been experienced in that a pipe wall is greatly thinned on the outer side of a bent portion, and in the worst case a pipe is ruptured. Everi in the case of not causing a rupture, a large rate of thinning of the pipe wall requires the use of a material having a greater thickness to satisfy the design stress, and therefore a sufficient reduction in weight: cannot be achieved.
As disclosed in Japanese Unexamined Patent Application Publication No. 55-56624, for example, it is known that improving an r-value (Lankford value) of a pipe in the axial direction is effective to overcome the problems described above. As a method for increasing the r-value of a steel pipe, however, it is only known to increase the r-value of strip steel as a base material of a steel pipe as disclosed in, for example, Japanese Unexamined Patent Application Publication No. 6-41689. When producing seam welded steel pipes, there has been a problem that the r-value is reduced in a portion where melting or transformation of a steel material has occurred during seam welding.
Another problem has arisen in that the seam welding cannot be applied to steel plates not having a high r-value, such as hot-rolled steel plates, high tensile strength steel plates, and low, medium and high carbon steel plates.
Accordingly, it is an object of the present invention to provide a steel pipe being superior in workability, particularly in bending workability, in which an r-value of the pipe in the axial direction in a portion where melting or transformation of a steel material has occurred during seam welding is as high as comparable to that in a portion where melting or transformation of the steel ma.terial has not occurred, and a method of producing the steel pipe.
Disclosure of Invention With the view of overcoming the problems mentioned above, the inventors have conducted studies based on a consideration that working and heat treatment of seam welded steel pipes are required to improve the r-value in a welded portion near the seam. Then, the inventors have studied a method of performing working and heat treatment of a steel pipe evenly at any positions in the circumferential direction, the steel pipe being produced by seam-welding cold-rolled steel having a high r-value. In the process of the studies, the inventors have found that the r-value of the seam welded steel pipe in the longitudinal direction (in the axial direction of the pipe) is noticeably improved to 1.2 or above, in particular to 1.6 or above, at any positions in the circumferential direction, including a seamed portion, by a method of performing diameter-reducing rolling on the seam welded steel pipe in a temperature range of from 600 C to AcJ with a reduction in diameter of not less than 30% (referred to as a "method according to the present invention"
HIGH-WORKABILITY STEEL PIPE AND METHOD OF PRODUCING
SAME
Technical Field The present invention relates to a steel pipe having superior workability and a method of producing the steel pipe.
Background Art For the purpose of reducing the weight and cost, the application of seam (electric resistance) welded steel pipes to automobile parts has been considered.
Conventional seam welded stee.l pipes, however, have not been sufficient in workability. Bending is employed to manufacture, e.g., undercarriage or suspension parts of automobiles. When the conventional seam welded steel pipes are subjected to the bending, a problem has been experienced in that a pipe wall is greatly thinned on the outer side of a bent portion, and in the worst case a pipe is ruptured. Everi in the case of not causing a rupture, a large rate of thinning of the pipe wall requires the use of a material having a greater thickness to satisfy the design stress, and therefore a sufficient reduction in weight: cannot be achieved.
As disclosed in Japanese Unexamined Patent Application Publication No. 55-56624, for example, it is known that improving an r-value (Lankford value) of a pipe in the axial direction is effective to overcome the problems described above. As a method for increasing the r-value of a steel pipe, however, it is only known to increase the r-value of strip steel as a base material of a steel pipe as disclosed in, for example, Japanese Unexamined Patent Application Publication No. 6-41689. When producing seam welded steel pipes, there has been a problem that the r-value is reduced in a portion where melting or transformation of a steel material has occurred during seam welding.
Another problem has arisen in that the seam welding cannot be applied to steel plates not having a high r-value, such as hot-rolled steel plates, high tensile strength steel plates, and low, medium and high carbon steel plates.
Accordingly, it is an object of the present invention to provide a steel pipe being superior in workability, particularly in bending workability, in which an r-value of the pipe in the axial direction in a portion where melting or transformation of a steel material has occurred during seam welding is as high as comparable to that in a portion where melting or transformation of the steel ma.terial has not occurred, and a method of producing the steel pipe.
Disclosure of Invention With the view of overcoming the problems mentioned above, the inventors have conducted studies based on a consideration that working and heat treatment of seam welded steel pipes are required to improve the r-value in a welded portion near the seam. Then, the inventors have studied a method of performing working and heat treatment of a steel pipe evenly at any positions in the circumferential direction, the steel pipe being produced by seam-welding cold-rolled steel having a high r-value. In the process of the studies, the inventors have found that the r-value of the seam welded steel pipe in the longitudinal direction (in the axial direction of the pipe) is noticeably improved to 1.2 or above, in particular to 1.6 or above, at any positions in the circumferential direction, including a seamed portion, by a method of performing diameter-reducing rolling on the seam welded steel pipe in a temperature range of from 600 C to AcJ with a reduction in diameter of not less than 30% (referred to as a "method according to the present invention"
hereinafter).
As a result of applying the method according to the present invention to seam welded steel pipes produced using various kinds of steel plates as base-material strip steel, the inventors have also found that a high r-value can be obtained regardless of the r-value of the original strip steel. Further, it has been found that with the method according to the present invention, the restriction of ingredients which has hitherto been employed to obtain a high r-value in steel sheets, i.e., a reduction of the C and N contents and addition of stabilizing elements such as Ti and Nb, are not required. As a result, seam welded steel pipes having a high r-value can also be produced using, as base-material strip steel, hot-rolled steel, high tensile strength steel such as dual phase steel, and low, medium and high carbon steel, which have a difficulty in achieving a high r-value in the stage of strip steel.
The views of the inventors regarding the reason why a steel pipe having a high r-value can be obtained from even a steel plate not having a high r-value are as follows.
By performing the diameter-reducing rolling on a seam welded steel pipe in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30%, an ideal aggregation structure due to the rolling, in which the <110> axis is parallel to the longitudinal direction and the <111> to <110> axes are parallel to the radial direction, is formed and then further developed through restoration and recrystallization. That aggregation structure provides a high r-value. The aggregation structure due to the rolling produces very great driving forces because crystals are rotated by workirig strains. Unlike an aggregation structure that is created through recrystallization in the case of obtaining a high r-value in steel sheets, the aggregation structure due to the rolling is less affected by the second phase and solid solution C. Consequently, even for the type of strip steel which has a difficulty in obtaining a high r-value in the stage of producing steel plates, a high r-value can be obtained in the stage of producing steel pipes.
Also, the reason why a high r-value is not obtained by performing the diameter-reducing rolling at low temperatures is that ideal crystal rotation is not caused because of high work hardness, or that restoration and recrystallization are not developed at a sufficient level because of low temperatures.
As a result of applying the method according to the present invention to seam welded steel pipes produced using various kinds of steel plates as base-material strip steel, the inventors have also found that a high r-value can be obtained regardless of the r-value of the original strip steel. Further, it has been found that with the method according to the present invention, the restriction of ingredients which has hitherto been employed to obtain a high r-value in steel sheets, i.e., a reduction of the C and N contents and addition of stabilizing elements such as Ti and Nb, are not required. As a result, seam welded steel pipes having a high r-value can also be produced using, as base-material strip steel, hot-rolled steel, high tensile strength steel such as dual phase steel, and low, medium and high carbon steel, which have a difficulty in achieving a high r-value in the stage of strip steel.
The views of the inventors regarding the reason why a steel pipe having a high r-value can be obtained from even a steel plate not having a high r-value are as follows.
By performing the diameter-reducing rolling on a seam welded steel pipe in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30%, an ideal aggregation structure due to the rolling, in which the <110> axis is parallel to the longitudinal direction and the <111> to <110> axes are parallel to the radial direction, is formed and then further developed through restoration and recrystallization. That aggregation structure provides a high r-value. The aggregation structure due to the rolling produces very great driving forces because crystals are rotated by workirig strains. Unlike an aggregation structure that is created through recrystallization in the case of obtaining a high r-value in steel sheets, the aggregation structure due to the rolling is less affected by the second phase and solid solution C. Consequently, even for the type of strip steel which has a difficulty in obtaining a high r-value in the stage of producing steel plates, a high r-value can be obtained in the stage of producing steel pipes.
Also, the reason why a high r-value is not obtained by performing the diameter-reducing rolling at low temperatures is that ideal crystal rotation is not caused because of high work hardness, or that restoration and recrystallization are not developed at a sufficient level because of low temperatures.
Furthermore, the reason why a high r-value is not obtained by a method of performing the diameter-reducing rolling on a steel pipe at low temperatures and then annealing the rolled steel pipe for recrystallization is that the desired aggregation structure is not developed through the cold rolling and the recrystallization because of the effect of the second phase and solid solution C.
In the field of producing steel sheets, there is known a method of producizzg a steel sheet having a high r-value by rolling steel into a sheet in the hot ferrite range. This method of producing a steel sheet having a high r-value is featured in that steel containing C and N in reduced amounts and added with stabilizing elements such as Ti and Nb is rolled at low temperatures and then recrystallized. That sheet rolling at low temperatures differs from the diameter-reducing rolling at high temperatures intended by the method according to the present invention. In fact, if the known sheet rolling in the hot ferrite range is carried out at 600 C or above, the r-value is not improved, but rather noticeably lowered on the contrary.
This is because, in the sheet rolling in which draft is applied in the thickness direction of a sheet, strain occurs in a direction different from that in the diameter-reducing rolling of a steel pipe in which draft is applied in the circumferential direction, and hence the aggregation structure effective in increasing the r-value is not developed.
As a result of further continuing the studies, the inventors have found that, in the method according to the present invention, the thickness deviation can be noticeably reduced and the occurrence of wrinkles near the seam can be suppressed by heating a seam welded steel pipe to temperatures of not lower than Ac, before the diameter-reducing rolling for austenitic transformation of a part or the whole of a steel structure, because the difference in mechanical properties between the hardened structure of the seam and the remaining portion is reduced. The present invention has been accomplished based on the findings set torth above. The features of the present invention are as follows.
(1) A high-workability steel pipe wherein an r-value in the longitudinal direction is not less than 1.2, more preferably not less than 1.6, over an entire area in the circumferential direction, including a seamed portion.
(2) A method of producing a high-workability steel pipe, the method comprising the step of performing diameter-reducing rolling on a steel pipe in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30%, the steel pipe being produced by seam-welding strip steel.
(3) A method of producing a high-workability steel pipe, wherein said method comprises the steps of heating a steel pipe to temperatures of not lower than Acl, said steel pipe being produced by seam-welding strip steel, and then immediately or after cooling and reheating said steel pipe, performing diameter- reducing rolling in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30% and after diameter-reducing rolling of said steel pipe, heat treatment of said rolled steel pipe by holding said pipe in a temperature range of from 600 C to 900 C for a time of 1 second or longer is performed during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after said cooling, said steel pipe being produced by seam-welding strip steel.
Brief Description of the Drawings Fig. 1 is a graph showing the relationship between an r-value in the longitudinal direction of a steel pipe having been subjected to diameter-reducing rolling and a reduction in diameter.
Fig. 2 is a graph showing the relationship between an r-value in the longitudinal direction of a steel pipe having been subjected to diameter-reducing rolling and an outgoing-side temperature in the rolling process.
Fig. 3 is a graph showing the relationship between a seam thickness deviation in a steel pipe having been subjected to diameter-reducing rolling and a heating temperature before the diameter-reducing rolling.
Best Mode for Carrying Out the Invention In a high-workability steel pipe according to the present invention, an r-value in the longitudinal direction is not less than 1.2. The reason is that the bending workability of the steel pipe is noticeably improved when the r-value is not less than 1.2. More preferably, the high-workability steel pipe has an r-value of not less than 1.6 because the bending workability is further improved when the r-value is not less than 1.6.
The high-workability steel pipe according to the present invention can be produced by performing diameter-reducing rolling on a steel pipe in a temperature range of from 600 C to Ac, with a reduction in diameter of not less than 30%, the steel pipe being produced by seam-welding strip steel and having a seam.
The r-value is affected by the reduction in diameterand the temperature during the diameter-reducing rolling.
Fig. 1 is a graph showing the relationship between the r-value in the longitudinal direction and the reduction in diameterresulted at circumferential positions 0 , 90 , 180 and 270 of each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under a condition of the outgoing-side temperature being set to 730 C
while changing the reduction in diameterthe seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel A in Table 1 given below. The seam position is assumed to be at 0 (this is similarly applied to the following description). From Fig. 1, it is understood that, regardless of the circumferential positions, the r-value of not less than 1.3 is obtained at the reduction in diameterof not less than 30%, and the r-value of not 2G less than 1.6 is obtained at the reduction in diameterof not less than 50%.
Fig. 2 is a graph showing the relationship between the r-value in the longitudinal direction and the outgoing-side temperature resulted at circumferential positions 0 , 90 , 180 and 270 of each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under a condition of the reduction in diameter set to 30% while changing the outgoing-side temperature, the seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel A in Table 1 given below. From Fig. 2, it is understood that the r-value of not less than 1.2 is obtained at the outgoing-side temperature of not lower than 600 C.
Based on the experiment results mentioned above, a lower limit of the temperature for the diameter-reducing rolling was set to 600 C and a lower limit of the reduction in diameterwas set to 30%. Also, an upper limit of the temperature for the diameter-reducing rolling was set to the same as an upper limit of the temperature range in which the steel structure contains ferrite, i.e., the temperature Ac,. The r-value is not improved even by the diameter-reducing rolling if it is performed on steel whose structure contains no ferrite. The temperature Ac, depends on the chemical composition of steel, and can be determined based on experiments. A range of temperature Ac3 is approximately not higher than 900 C.
In the present invention, so long as the steel structure contains ferrite, the second phase (phase other than ferrite) is not. limited to particular one.
For example, austeriite may be the second phase. More preferably, the diameter-reducing rolling is performed at temperatures where ferrite forms the main phase (phase having a volume ratio of 50% or more).
The gist of the present invention resides in that a steel pipe is subjected to the diameter-reducing rolling in a temperature range where the steel structure has the ferrite phase. From the standpoint of improving the r-value, there is no particular restriction upon the history prior to the diameter-reducing rolling. For example, the heating temperature prior to the diameter-reducing rolling may be any of the temperature at which the steel structure has the single austenitic phase, the temperature at which the steel structure has the two austenitic and ferrite phases, and the temperature at which the steel structure has the single ferrite phase. Further, prior to the diameter-reducing rolling, the steel pipe may be rolled at such temperatures as forming austenite as the single phase or the main phase.
Fig. 3 is a graph showing the relationship between a heating temperature and a thickness deviation resulted for each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under conditions of the reduction in diameter set to 30% and the rolling temperature set to 700 C while changing the heating temperature, the seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel D
in Table 1 given below. From Fig. 3, it is understood that the heating prior to the diameter-reducing rolling is preferably set to be not lower than the temperature Acl from the standpoint of suppressing the thickness deviation and wrinkles occurred near the seam. The temperature Acl depends on the chemical composition of the steel pipe, etc., and can be determined based on experiments. A range of temperature Acl is approximately not lower than 800 C. However, if the heating temperature is too high, the crystal grain size would be excessively increased, thus resulting in a problem of, for example, increasing surface roughness during the working. For that reason, the heating temperature is preferably set to be not higher than 900 C.
There is no particular restriction upon the cooling after the heating of the steel pipe. Subsequent to the heating, the diameter-reducing rolling may be performed, for example, after cooling the steel pipe down to temperatures at which ferrite forms the main phase, or by reheating the steel pipe after cooling it down to the room temperature.
Further, preferably, after the diameter-reducing rolling of the steel pipe, heat treatment of holding the rolled steel pipe in a temperature range of from 600 C to 900 C for a time of 1 second or longer is performed in the present invention.
In the present invention, since the diameter-reducing rolling is performed at temperatures of not lower than 600 C, the work hardness is low and a sufficient level of workability is obtained with additional treatment. Even so, by performing heat treatment for holding the rolled steel pipe at a certain temperature for a certain time in succession to the diameter-reducing rolling, the elongation and the r-value are further improved. This effect is developed by holding the rolled steel pipe at temperatures of not lower than 600 C for a time of 1 second or longer.
However, if the holding temperature exceeds 900 C, the steel structure would be transformed into the single austenitic phase and the r-value would be reduced because of the randomized aggregation structure. For that reason, the heat treatmerit is preferably performed on conditions of the holding temperature in the range of from 600 C to 900 C and the holding time of 1 second or longer. Additionally, the heat treatment may be performed during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after the cooling_ (Example) Seam welded steel pipes were produced by an ordinary method from various }cinds of hot-rolled steel plates having chemical compositions shown in Table 1, and the diameter-reducing rol:ling was,performed on each steel pipe under conditions shown in Table 2. Heating of the steel pipe prior to the diameter-reducing rolling was not held at all or held for a time of 1 to 600 seconds after reaching thE: temperature shown in - Table 2. Tensile specimens of JIS No. 12-A were sampled from circumferential positions 0 , 90 , 1$0 and 270 of each steel pipe obtained_ After bonding a strain gauge with a gauge-length of 2 mm to each specimen, a tensile test was carried out on the specimen by applying a nominal strain of 6 to 7%. Then, a ratio of a true strain F, in the longitudinal direction to a true strain e~ in the width direction;was measured. From a gradient p of that ratio, the r-value was calculated based on the following formulae:
pE~
r-value = p/(-1 - p) 1.5 Further, a thickness deviation il was calculated by measuring a pipe wall thickriess ts of a seamed portion and an average pipe wall thickness tb of the remaining portion. That is:
thickness deviation 11% = (ts - tb)/tb x 100%
Moreover, the presence or absence of wrinkles was determined by observing an image of an area near the seam in a cross-section perpendicular to the axis of the steel pipe, the image being enlarged at a magnification of 50 times.
Those results are listed in Table 3 along with the tensile strength (TS) and the elongation (El).
The r-value is 1.2 or above at any positions in the circumferential direction in Examples of the present invention, whereas the r-value is below 1.2 in Comparative Examples. Also, in the specimens heated to temperatures of not lower thari Acx, the thickness deviation is smaller and wrinkles are not caused.
Industrial Applicability According to the present invention, a high-workability steel pipe can be provided which has a high r-vaiue over an entire area iri the circumferential direction, including a seamed portion, and also has a good shape. Limits in bending and expanding work of the steel pipe are noticeably improved, whereby omission of steps due to the integral forming and a reduction in weight can be achieved. Further, seam welded steel pipes having a high r-value can also be produced using, as base materials, hot--rolled steel, high tensile strength steel such as dual phase steel, and low, medium and high carbon steel, which have a difficulty in achieving a high r-value with a conventional method of producing a steel pipe by simply seam-welding a steel plate. As a result, the present invention is able to remarkably enlarge the applicable range of bending of steel pipes and hence greatly contributes to development of the industry.
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rt +J 4 PO U fa W W~ c71 x~ H>,j ~G ~~ a H cn Table 2 No Steel Heating Incoming- Outgoing- Total Effective Heat Remarks Temperature side side Reduction Reduction Treatment ( C) Temperature Temperature in in in Diameter- in Diameter- Diameter Diameter*
Reducing Reducing (k) (8) Rolling ( C) Rollin ( C) 1 A 800 780 730 50 50 - Example 2 A 900 880 830 50 5 - Comparative Example 3 A 630 610 560 50 10 - Comparative Example 4 B 800 780 730 50 50 - Example B 800 780 730 50 50 - Example 6 C 800 780 730 50 50 730 C x 5 Example min.
7 D 900** 720 680 50 50 - Example 8 D 850 720 680 50 50 - Example 9 D 800 780 730 50 50 - Example D 800 720 680 50 50 - Example 11 D 750 720 680 50 50 - Example 12 D 735 720 680 50 50 - Example 13 D 720 720 680 50 50 - Example 14 E 800 780 730 50 50 - Example F 800 780 730 0 0 - Comparative Example 1 16 F 800 780 730 15 15 - Comparative Example 17 F 800 780 730 30 30 - Example 18 F 800 780 730 40 40 - Example 19 F 800 780 730 50 1 50 - Example F 800 780 730 60 60 - Example 21 F 800 780 73070 70 - Example 22 F 900 890 850 30 2 - Comparative Exa le 3 I F 850 840 780 30 30 - Example 24 F 750 730 680 30 30 - Example F 700 680 600 30 30 - Example 26 F 630 610 560 50 10 - Comparative Example 27 G 900 780 _730 50 50 - Example 28 G 850 780 730 50 50 - Example 29 G 800 780 730 30 30 - Example 30G 800 780 730 40 40 - Example 31 G 800 780 730 50 50 - Example 32 H 800 780 730 50 50 - Example 33 I 800 780 730 50 50 - Example 34 J 800 780 73050 50 - Example 351K 800 780 730 50 50 - Example 36 L 760 740 700 60 60 - Example - _ ----' * effective reduction in diameter: reduction in diameter in temperature range of 600 C to Ao3 ** rolling after cooling and reheating (for other types of steel, rolling immediately after heating) Table 3 Seam Wrinklea No 0 (Seam) 90 180 270 Thick 0 not Remarks nees occurred Devia tion TS/ E1* r- TS/ E1' r- TS/M El' r- TS/ E1* r- /4 x MPa /i value MPa /t value Pa /t value MPa /! value occurred 1 300 55 2.0 303 54 2.0 307 54 2.1 301 55 2.1 0.3 O Example 2 300 45 0.8 309 45 0.9 307 45 0.8 308 45 0.8 0.3 0 Compara tive Example 3 450 35 1.0 450 35 1.1 459 36 1.0 451 34 1.1 10.D x Compara tive Example 4 350 50 2.0 356 51 2.0 356 50 2.0 350 51 2.0 0.5 O Example 350 50 2.4 358 51 2.4 351 49 2.5 356 49 2.4 0.5 O Example 6 620 25 1.8 624 24 1.8 625 25 1.8 629 25 1.9 0.3 O Example 7 640 27 1.7 646 27 1.7 641 27 1.7 647 26 1.7 0.5 0 Example 8 631 25 1.7 651 26 1.6 641 25 1.8 641 25 1.8 1.0 O Example 9 620 28 1.8 626 29 1.8 621 29 1.9 627 28 1.9 0.5 O Example 640 24 1.6 659 24 1.7 632 24 1.7 636 24 1.7 2.0 0 Example 11 644 22 1.6 650 22 1.7 635 22 1.7 632 22 1.8 3.0 O Example 12 653 20 1.6 657 21 1.6 640 21 1.8 623 21 1.8 8.0 x Example 13 644 19 1.7 650 19 1.7 637 19 1.9 614 19 1.8 15.0 x Example 14 650 25 1.8 652 25 1.9 651 25 1.8 651 26 1.9 0.5 O Example 500 25 0.7 508 26 0.8 503 24 0.8 501 25 0.8 0.3 O compara tive Exam le 16 590 28 1.0 593 28 1.1 599 29 1.1 595 28 1.0 0.3 O Co~pVea Example 17 610 28 1.3 610 28 1.3 618 28 1.3 614 29 1.3 0.9 O Example 18 610 29 1.4 619 29 1.4 611 30 1.4 611 28 1.4 0.9 O Example 19 610 30 1.6 617 31 1.7 611 30 1.6 615 31 1.6 0.9 O Example 610 32 2.0 616 31 2.0 612 33 2.1 610 31 2.1 0.9 0 Example 21 610 35 2.5 615 35 2.6 613 35 2.6 618 36 2.6 0.8 O Example 22 590 28 0.8 593 27 0.8 599 28 0.8 593 28 0.9 0.2 0 Compara tive Example 23 610 29 1.4 612 30 1.4 614 30 1.5 616 29 1.5 0.2 O Example 24 610 28 1.3 613 29 1.3 615 28 1.4 612 28 1.4 0.0 O Example 650 27 1.2 651 26 1.2 650 27 1.2 658 26 1.2 3.0 x Example 26 630 22 0.9 680 21 1.0 687 22 1.0 685 23 0.9 15.0 x Compara tive Example 27 630 30 1.3 638 30 1.3 639 31 1.4 640 31 1.3 0.7 O Example 28 630 33 1.4 636 33 1.4 630 33 1.5 638 33 1.5 0.5 O Example 29 630 30 1.3 638 30 1.3 639 31 1.4 i 640 31 1.3 0.3 O Example 630 33 1.4 636 33 1.4 630 33 1.5 638 33 1.5 0.3 0 Example 31 630 35 1.8 637 34 1.9 635 35 1.8 633 34 1.9 0.4 O Example 32 600 30 1.8 606 30 1.8 609 30 1.9 600 30 1.8 0.5 0 Example 33 600 30 1.8 604 29 1.8 605 31 1.9 601 29 1.9 0.8 O Example 34 820 24 1.6 823 25 1.6 821 25 1.7 825 24 1.7 0.3 0 Example 820 22 1.6 821 22 1.6 823 1.7 830 22 1.7 0.8 0 Example 36 695 28 1.8 595 28 1.8 595 28 1,8 595 28 1.8 0.3 O Example * yheet thickness - 1.6 mm
In the field of producing steel sheets, there is known a method of producizzg a steel sheet having a high r-value by rolling steel into a sheet in the hot ferrite range. This method of producing a steel sheet having a high r-value is featured in that steel containing C and N in reduced amounts and added with stabilizing elements such as Ti and Nb is rolled at low temperatures and then recrystallized. That sheet rolling at low temperatures differs from the diameter-reducing rolling at high temperatures intended by the method according to the present invention. In fact, if the known sheet rolling in the hot ferrite range is carried out at 600 C or above, the r-value is not improved, but rather noticeably lowered on the contrary.
This is because, in the sheet rolling in which draft is applied in the thickness direction of a sheet, strain occurs in a direction different from that in the diameter-reducing rolling of a steel pipe in which draft is applied in the circumferential direction, and hence the aggregation structure effective in increasing the r-value is not developed.
As a result of further continuing the studies, the inventors have found that, in the method according to the present invention, the thickness deviation can be noticeably reduced and the occurrence of wrinkles near the seam can be suppressed by heating a seam welded steel pipe to temperatures of not lower than Ac, before the diameter-reducing rolling for austenitic transformation of a part or the whole of a steel structure, because the difference in mechanical properties between the hardened structure of the seam and the remaining portion is reduced. The present invention has been accomplished based on the findings set torth above. The features of the present invention are as follows.
(1) A high-workability steel pipe wherein an r-value in the longitudinal direction is not less than 1.2, more preferably not less than 1.6, over an entire area in the circumferential direction, including a seamed portion.
(2) A method of producing a high-workability steel pipe, the method comprising the step of performing diameter-reducing rolling on a steel pipe in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30%, the steel pipe being produced by seam-welding strip steel.
(3) A method of producing a high-workability steel pipe, wherein said method comprises the steps of heating a steel pipe to temperatures of not lower than Acl, said steel pipe being produced by seam-welding strip steel, and then immediately or after cooling and reheating said steel pipe, performing diameter- reducing rolling in a temperature range of from 600 C to Ac3 with a reduction in diameter of not less than 30% and after diameter-reducing rolling of said steel pipe, heat treatment of said rolled steel pipe by holding said pipe in a temperature range of from 600 C to 900 C for a time of 1 second or longer is performed during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after said cooling, said steel pipe being produced by seam-welding strip steel.
Brief Description of the Drawings Fig. 1 is a graph showing the relationship between an r-value in the longitudinal direction of a steel pipe having been subjected to diameter-reducing rolling and a reduction in diameter.
Fig. 2 is a graph showing the relationship between an r-value in the longitudinal direction of a steel pipe having been subjected to diameter-reducing rolling and an outgoing-side temperature in the rolling process.
Fig. 3 is a graph showing the relationship between a seam thickness deviation in a steel pipe having been subjected to diameter-reducing rolling and a heating temperature before the diameter-reducing rolling.
Best Mode for Carrying Out the Invention In a high-workability steel pipe according to the present invention, an r-value in the longitudinal direction is not less than 1.2. The reason is that the bending workability of the steel pipe is noticeably improved when the r-value is not less than 1.2. More preferably, the high-workability steel pipe has an r-value of not less than 1.6 because the bending workability is further improved when the r-value is not less than 1.6.
The high-workability steel pipe according to the present invention can be produced by performing diameter-reducing rolling on a steel pipe in a temperature range of from 600 C to Ac, with a reduction in diameter of not less than 30%, the steel pipe being produced by seam-welding strip steel and having a seam.
The r-value is affected by the reduction in diameterand the temperature during the diameter-reducing rolling.
Fig. 1 is a graph showing the relationship between the r-value in the longitudinal direction and the reduction in diameterresulted at circumferential positions 0 , 90 , 180 and 270 of each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under a condition of the outgoing-side temperature being set to 730 C
while changing the reduction in diameterthe seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel A in Table 1 given below. The seam position is assumed to be at 0 (this is similarly applied to the following description). From Fig. 1, it is understood that, regardless of the circumferential positions, the r-value of not less than 1.3 is obtained at the reduction in diameterof not less than 30%, and the r-value of not 2G less than 1.6 is obtained at the reduction in diameterof not less than 50%.
Fig. 2 is a graph showing the relationship between the r-value in the longitudinal direction and the outgoing-side temperature resulted at circumferential positions 0 , 90 , 180 and 270 of each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under a condition of the reduction in diameter set to 30% while changing the outgoing-side temperature, the seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel A in Table 1 given below. From Fig. 2, it is understood that the r-value of not less than 1.2 is obtained at the outgoing-side temperature of not lower than 600 C.
Based on the experiment results mentioned above, a lower limit of the temperature for the diameter-reducing rolling was set to 600 C and a lower limit of the reduction in diameterwas set to 30%. Also, an upper limit of the temperature for the diameter-reducing rolling was set to the same as an upper limit of the temperature range in which the steel structure contains ferrite, i.e., the temperature Ac,. The r-value is not improved even by the diameter-reducing rolling if it is performed on steel whose structure contains no ferrite. The temperature Ac, depends on the chemical composition of steel, and can be determined based on experiments. A range of temperature Ac3 is approximately not higher than 900 C.
In the present invention, so long as the steel structure contains ferrite, the second phase (phase other than ferrite) is not. limited to particular one.
For example, austeriite may be the second phase. More preferably, the diameter-reducing rolling is performed at temperatures where ferrite forms the main phase (phase having a volume ratio of 50% or more).
The gist of the present invention resides in that a steel pipe is subjected to the diameter-reducing rolling in a temperature range where the steel structure has the ferrite phase. From the standpoint of improving the r-value, there is no particular restriction upon the history prior to the diameter-reducing rolling. For example, the heating temperature prior to the diameter-reducing rolling may be any of the temperature at which the steel structure has the single austenitic phase, the temperature at which the steel structure has the two austenitic and ferrite phases, and the temperature at which the steel structure has the single ferrite phase. Further, prior to the diameter-reducing rolling, the steel pipe may be rolled at such temperatures as forming austenite as the single phase or the main phase.
Fig. 3 is a graph showing the relationship between a heating temperature and a thickness deviation resulted for each steel pipe which was produced by performing the diameter-reducing rolling on a seam welded steel pipe under conditions of the reduction in diameter set to 30% and the rolling temperature set to 700 C while changing the heating temperature, the seam welded steel pipe being produced by an ordinary method from strip steel having the same composition as steel D
in Table 1 given below. From Fig. 3, it is understood that the heating prior to the diameter-reducing rolling is preferably set to be not lower than the temperature Acl from the standpoint of suppressing the thickness deviation and wrinkles occurred near the seam. The temperature Acl depends on the chemical composition of the steel pipe, etc., and can be determined based on experiments. A range of temperature Acl is approximately not lower than 800 C. However, if the heating temperature is too high, the crystal grain size would be excessively increased, thus resulting in a problem of, for example, increasing surface roughness during the working. For that reason, the heating temperature is preferably set to be not higher than 900 C.
There is no particular restriction upon the cooling after the heating of the steel pipe. Subsequent to the heating, the diameter-reducing rolling may be performed, for example, after cooling the steel pipe down to temperatures at which ferrite forms the main phase, or by reheating the steel pipe after cooling it down to the room temperature.
Further, preferably, after the diameter-reducing rolling of the steel pipe, heat treatment of holding the rolled steel pipe in a temperature range of from 600 C to 900 C for a time of 1 second or longer is performed in the present invention.
In the present invention, since the diameter-reducing rolling is performed at temperatures of not lower than 600 C, the work hardness is low and a sufficient level of workability is obtained with additional treatment. Even so, by performing heat treatment for holding the rolled steel pipe at a certain temperature for a certain time in succession to the diameter-reducing rolling, the elongation and the r-value are further improved. This effect is developed by holding the rolled steel pipe at temperatures of not lower than 600 C for a time of 1 second or longer.
However, if the holding temperature exceeds 900 C, the steel structure would be transformed into the single austenitic phase and the r-value would be reduced because of the randomized aggregation structure. For that reason, the heat treatmerit is preferably performed on conditions of the holding temperature in the range of from 600 C to 900 C and the holding time of 1 second or longer. Additionally, the heat treatment may be performed during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after the cooling_ (Example) Seam welded steel pipes were produced by an ordinary method from various }cinds of hot-rolled steel plates having chemical compositions shown in Table 1, and the diameter-reducing rol:ling was,performed on each steel pipe under conditions shown in Table 2. Heating of the steel pipe prior to the diameter-reducing rolling was not held at all or held for a time of 1 to 600 seconds after reaching thE: temperature shown in - Table 2. Tensile specimens of JIS No. 12-A were sampled from circumferential positions 0 , 90 , 1$0 and 270 of each steel pipe obtained_ After bonding a strain gauge with a gauge-length of 2 mm to each specimen, a tensile test was carried out on the specimen by applying a nominal strain of 6 to 7%. Then, a ratio of a true strain F, in the longitudinal direction to a true strain e~ in the width direction;was measured. From a gradient p of that ratio, the r-value was calculated based on the following formulae:
pE~
r-value = p/(-1 - p) 1.5 Further, a thickness deviation il was calculated by measuring a pipe wall thickriess ts of a seamed portion and an average pipe wall thickness tb of the remaining portion. That is:
thickness deviation 11% = (ts - tb)/tb x 100%
Moreover, the presence or absence of wrinkles was determined by observing an image of an area near the seam in a cross-section perpendicular to the axis of the steel pipe, the image being enlarged at a magnification of 50 times.
Those results are listed in Table 3 along with the tensile strength (TS) and the elongation (El).
The r-value is 1.2 or above at any positions in the circumferential direction in Examples of the present invention, whereas the r-value is below 1.2 in Comparative Examples. Also, in the specimens heated to temperatures of not lower thari Acx, the thickness deviation is smaller and wrinkles are not caused.
Industrial Applicability According to the present invention, a high-workability steel pipe can be provided which has a high r-vaiue over an entire area iri the circumferential direction, including a seamed portion, and also has a good shape. Limits in bending and expanding work of the steel pipe are noticeably improved, whereby omission of steps due to the integral forming and a reduction in weight can be achieved. Further, seam welded steel pipes having a high r-value can also be produced using, as base materials, hot--rolled steel, high tensile strength steel such as dual phase steel, and low, medium and high carbon steel, which have a difficulty in achieving a high r-value with a conventional method of producing a steel pipe by simply seam-welding a steel plate. As a result, the present invention is able to remarkably enlarge the applicable range of bending of steel pipes and hence greatly contributes to development of the industry.
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rt +J 4 PO U fa W W~ c71 x~ H>,j ~G ~~ a H cn Table 2 No Steel Heating Incoming- Outgoing- Total Effective Heat Remarks Temperature side side Reduction Reduction Treatment ( C) Temperature Temperature in in in Diameter- in Diameter- Diameter Diameter*
Reducing Reducing (k) (8) Rolling ( C) Rollin ( C) 1 A 800 780 730 50 50 - Example 2 A 900 880 830 50 5 - Comparative Example 3 A 630 610 560 50 10 - Comparative Example 4 B 800 780 730 50 50 - Example B 800 780 730 50 50 - Example 6 C 800 780 730 50 50 730 C x 5 Example min.
7 D 900** 720 680 50 50 - Example 8 D 850 720 680 50 50 - Example 9 D 800 780 730 50 50 - Example D 800 720 680 50 50 - Example 11 D 750 720 680 50 50 - Example 12 D 735 720 680 50 50 - Example 13 D 720 720 680 50 50 - Example 14 E 800 780 730 50 50 - Example F 800 780 730 0 0 - Comparative Example 1 16 F 800 780 730 15 15 - Comparative Example 17 F 800 780 730 30 30 - Example 18 F 800 780 730 40 40 - Example 19 F 800 780 730 50 1 50 - Example F 800 780 730 60 60 - Example 21 F 800 780 73070 70 - Example 22 F 900 890 850 30 2 - Comparative Exa le 3 I F 850 840 780 30 30 - Example 24 F 750 730 680 30 30 - Example F 700 680 600 30 30 - Example 26 F 630 610 560 50 10 - Comparative Example 27 G 900 780 _730 50 50 - Example 28 G 850 780 730 50 50 - Example 29 G 800 780 730 30 30 - Example 30G 800 780 730 40 40 - Example 31 G 800 780 730 50 50 - Example 32 H 800 780 730 50 50 - Example 33 I 800 780 730 50 50 - Example 34 J 800 780 73050 50 - Example 351K 800 780 730 50 50 - Example 36 L 760 740 700 60 60 - Example - _ ----' * effective reduction in diameter: reduction in diameter in temperature range of 600 C to Ao3 ** rolling after cooling and reheating (for other types of steel, rolling immediately after heating) Table 3 Seam Wrinklea No 0 (Seam) 90 180 270 Thick 0 not Remarks nees occurred Devia tion TS/ E1* r- TS/ E1' r- TS/M El' r- TS/ E1* r- /4 x MPa /i value MPa /t value Pa /t value MPa /! value occurred 1 300 55 2.0 303 54 2.0 307 54 2.1 301 55 2.1 0.3 O Example 2 300 45 0.8 309 45 0.9 307 45 0.8 308 45 0.8 0.3 0 Compara tive Example 3 450 35 1.0 450 35 1.1 459 36 1.0 451 34 1.1 10.D x Compara tive Example 4 350 50 2.0 356 51 2.0 356 50 2.0 350 51 2.0 0.5 O Example 350 50 2.4 358 51 2.4 351 49 2.5 356 49 2.4 0.5 O Example 6 620 25 1.8 624 24 1.8 625 25 1.8 629 25 1.9 0.3 O Example 7 640 27 1.7 646 27 1.7 641 27 1.7 647 26 1.7 0.5 0 Example 8 631 25 1.7 651 26 1.6 641 25 1.8 641 25 1.8 1.0 O Example 9 620 28 1.8 626 29 1.8 621 29 1.9 627 28 1.9 0.5 O Example 640 24 1.6 659 24 1.7 632 24 1.7 636 24 1.7 2.0 0 Example 11 644 22 1.6 650 22 1.7 635 22 1.7 632 22 1.8 3.0 O Example 12 653 20 1.6 657 21 1.6 640 21 1.8 623 21 1.8 8.0 x Example 13 644 19 1.7 650 19 1.7 637 19 1.9 614 19 1.8 15.0 x Example 14 650 25 1.8 652 25 1.9 651 25 1.8 651 26 1.9 0.5 O Example 500 25 0.7 508 26 0.8 503 24 0.8 501 25 0.8 0.3 O compara tive Exam le 16 590 28 1.0 593 28 1.1 599 29 1.1 595 28 1.0 0.3 O Co~pVea Example 17 610 28 1.3 610 28 1.3 618 28 1.3 614 29 1.3 0.9 O Example 18 610 29 1.4 619 29 1.4 611 30 1.4 611 28 1.4 0.9 O Example 19 610 30 1.6 617 31 1.7 611 30 1.6 615 31 1.6 0.9 O Example 610 32 2.0 616 31 2.0 612 33 2.1 610 31 2.1 0.9 0 Example 21 610 35 2.5 615 35 2.6 613 35 2.6 618 36 2.6 0.8 O Example 22 590 28 0.8 593 27 0.8 599 28 0.8 593 28 0.9 0.2 0 Compara tive Example 23 610 29 1.4 612 30 1.4 614 30 1.5 616 29 1.5 0.2 O Example 24 610 28 1.3 613 29 1.3 615 28 1.4 612 28 1.4 0.0 O Example 650 27 1.2 651 26 1.2 650 27 1.2 658 26 1.2 3.0 x Example 26 630 22 0.9 680 21 1.0 687 22 1.0 685 23 0.9 15.0 x Compara tive Example 27 630 30 1.3 638 30 1.3 639 31 1.4 640 31 1.3 0.7 O Example 28 630 33 1.4 636 33 1.4 630 33 1.5 638 33 1.5 0.5 O Example 29 630 30 1.3 638 30 1.3 639 31 1.4 i 640 31 1.3 0.3 O Example 630 33 1.4 636 33 1.4 630 33 1.5 638 33 1.5 0.3 0 Example 31 630 35 1.8 637 34 1.9 635 35 1.8 633 34 1.9 0.4 O Example 32 600 30 1.8 606 30 1.8 609 30 1.9 600 30 1.8 0.5 0 Example 33 600 30 1.8 604 29 1.8 605 31 1.9 601 29 1.9 0.8 O Example 34 820 24 1.6 823 25 1.6 821 25 1.7 825 24 1.7 0.3 0 Example 820 22 1.6 821 22 1.6 823 1.7 830 22 1.7 0.8 0 Example 36 695 28 1.8 595 28 1.8 595 28 1,8 595 28 1.8 0.3 O Example * yheet thickness - 1.6 mm
Claims
1. A method of producing a high-workability steel pipe, wherein said method comprises the steps of heating a steel pipe to temperatures of not lower than Ac1, said steel pipe being produced by seam-welding strip steel, and then immediately or after cooling and reheating said steel pipe, performing diameter-reducing rolling in a temperature range of from 600°C to Ac3 with a reduction in diameter of not less than 30% and after diameter- reducing rolling of said steel pipe, heat treatment of said rolled steel pipe by holding said pipe in a temperature range of from 600°C to 900°C for a time of 1 second or longer is performed during cooling subsequent to the diameter-reducing rolling or by reheating the rolled steel pipe after said cooling, said steel pipe being produced by seam-welding strip steel.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/JP2001/005053 WO2002103069A1 (en) | 2000-01-28 | 2001-06-14 | Steel pipe having high formability and method for production thereof |
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| CA2403830C true CA2403830C (en) | 2009-06-30 |
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| EP (1) | EP1437422A4 (en) |
| CN (1) | CN1234896C (en) |
| BR (1) | BR0110441B1 (en) |
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| WO2006057098A1 (en) * | 2004-11-26 | 2006-06-01 | Jfe Steel Corporation | Steel pipe having excellent electromagnetic properties and process for producing the same |
| IN2014KN02910A (en) * | 2012-06-28 | 2015-05-08 | Jfe Steel Corp | |
| US10738366B2 (en) | 2013-12-20 | 2020-08-11 | Nippon Steel Corporation | Electric-resistance welded steel pipe |
| CA3030455C (en) * | 2016-07-14 | 2021-01-26 | Tata Steel Nederland Tubes Bv | Method for the in-line manufacturing of steel tube |
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| DE2900022C3 (en) * | 1979-01-02 | 1981-12-03 | Estel Hoesch Werke Ag, 4600 Dortmund | Process for producing profiles |
| JPH04143015A (en) * | 1990-10-05 | 1992-05-18 | Sumitomo Metal Ind Ltd | Manufacture of high tensile electric resistance welded tube having excellent toughness of welded part |
| JPH0641689A (en) * | 1992-06-22 | 1994-02-15 | Nippon Steel Corp | High cr steel tube excellent in workability |
| DE4318931C1 (en) * | 1993-06-03 | 1994-12-01 | Mannesmann Ag | Method for the production of welded tubes |
| JP3518247B2 (en) * | 1996-06-10 | 2004-04-12 | Ｊｆｅスチール株式会社 | Welded steel pipe and its manufacturing method |
| JP3481409B2 (en) * | 1996-12-17 | 2003-12-22 | 新日本製鐵株式会社 | Hydroforming method of steel pipe |
| US6290789B1 (en) * | 1997-06-26 | 2001-09-18 | Kawasaki Steel Corporation | Ultrafine-grain steel pipe and process for manufacturing the same |
| JP3785828B2 (en) * | 1998-09-21 | 2006-06-14 | Ｊｆｅスチール株式会社 | Steel pipe drawing method |
| JP3760640B2 (en) * | 1998-09-22 | 2006-03-29 | Ｊｆｅスチール株式会社 | Steel pipe manufacturing method |
| JP2000212694A (en) * | 1999-01-20 | 2000-08-02 | Nippon Steel Corp | Electric resistance welded tube excellent in workability and its production |
| JP2001162305A (en) * | 1999-12-08 | 2001-06-19 | Kawasaki Steel Corp | Manufacturing method of steel tube |
| JP3794230B2 (en) * | 2000-01-28 | 2006-07-05 | Ｊｆｅスチール株式会社 | Manufacturing method of high workability steel pipe |
| JP4571754B2 (en) * | 2001-03-13 | 2010-10-27 | 新日本製鐵株式会社 | Manufacturing method of steel pipe with excellent formability |
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| CA2403830A1 (en) | 2002-12-14 |
| BR0110441B1 (en) | 2013-06-18 |
| EP1437422A4 (en) | 2006-08-23 |
| EP1437422A1 (en) | 2004-07-14 |
| CN1234896C (en) | 2006-01-04 |
| WO2002103069A1 (en) | 2002-12-27 |
| BR0110441A (en) | 2003-07-01 |
| CN1426489A (en) | 2003-06-25 |
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