Patent Grant
9546408
The present invention relates to a method for quenching a steel tube or pipe (hereinafter, collectively referred to as “steel pipe”) made of medium or high carbon type of steel, etc., and more particularly to a method for quenching a steel pipe which can effectively prevent quench cracking of a steel pipe of low or medium alloy steel containing a medium or high level of carbon, or martensitic stainless steel pipe, which may generally be prone to quench cracking when quenched by rapid cooling means such as water quenching.
Unless otherwise stated, the definitions of terms herein are as follows.
The symbol “%” represents mass percentage of each component contained in an object such as medium or high carbon type of steel and martensitic stainless steel.
The term “low alloy steel” refers herein to steel in which amounts of alloy elements are not more than 5%.
The term “medium alloy steel” refers herein to steel in which amounts of alloy elements are in the range of 5% or more to 10% or less.
As one fundamental method to strengthen steel materials, methods of utilizing phase transformation by heat treatment, particularly martensitic transformation, have widely been practiced. Since a steel pipe made of medium carbon steel or high carbon steel (typically, a steel pipe of low alloy steel or medium alloy steel) exhibits excellent strength and toughness after being quenched and tempered, methods for strengthening steel materials by quenching and tempering have been used in many applications including machine structural members, and steel products for oil well use. The strength of steel can be remarkably increased by quenching, and this strengthening effect depends on C content in the steel. However, since martensite structure as quenched is generally brittle, it is subjected to tempering at a temperature not more than Ac1 transformation point after quenching, thereby improving its toughness.
To obtain a martensite structure by quenching low alloy steel or medium alloy steel, rapid cooling such as water quenching is necessary. If cooling rate is insufficient, a structure softer than martensite, such as bainite, would be mixed with martensite so that sufficient quenching effect cannot be achieved.
In quenching treatment of steel materials, quench cracking may become an issue. As described above, when a steel product is rapidly cooled, it is inevitably impossible to uniformly cool the entire steel product, and then thermal stress is generated in the steel product, attributable to the difference in the contraction rate between an early cooled portion and a late cooled portion. Further, when a quenching treatment causes martensitic transformation, transformation stress is generated as a result of occurrence of volume expansion due to transformation from austenite to martensite. The volume expansion depends on a C content in steel, and the more the C content is, the larger the volume expansion becomes. Therefore, the steel having a high C content is prone to have large transformation stress in a quenching stage, and is highly likely to cause quench cracking.
In particular, when the steel product to be quenched has a tubular shape, it exhibits a very complex stress state, compared to other shapes such as flat plate shape, or a bar/wire shape. For this reason, if a tubular steel product having a high C content is subjected to rapid cooling, such as water quenching, crack susceptibility remarkably increases and quench cracking frequently occurs, resulting in a very poor yield of the product.
Therefore, when a steel pipe containing a high carbon among low alloy steels and medium alloy steels is quenched, the cooling rate during the quenching treatment is controlled by performing oil quenching which has a lower cooling capacity compared to water quenching, or performing relatively slow cooling by mist cooling, in order to prevent quench cracking and increase the yield of product.
However, when such quenching means is adopted, a sufficient amount of martensite structure cannot be obtained, resulting in a mixed microstructure including a considerable amount of bainite which occurs at a comparatively elevated temperature. For that reason, there arises a problem that even if quenching and tempering is applied, it is not possible to fully make use of excellent toughness of tempered martensite structure, thereby resulting in deterioration of high toughness of a product steel pipe.
While martensite structure is capitalized in a steel pipe of low alloy steel or medium alloy steel as described above, a martensitic stainless steel pipe, which can easily achieve high strength, is widely used in the field of a stainless steel pipe as well for various applications for which strength and corrosion resistance are required. Particularly in recent years, from energy-related circumstances, martensitic stainless steel pipes are extensively used as oil well country goods for collecting oil and natural gas.
That is, the environment of wells (oil wells) for collecting oil and natural gas has become more and more hostile in recent years, and in addition to the increase of pressure associated with the increase of drilling depth, the number of wells which contain significant amounts of corrosive components such as wet carbon dioxide gas, hydrogen sulfide, and chlorine ions have been increasing. Accordingly, while the increase of the strength of material is demanded, corrosion of the material due to corrosive components as described above and embrittlement caused thereby have become an issue, and thus there is a growing demand for oil well pipes having excellent corrosion resistance.
Under such circumstances, martensitic stainless steels are widely used in environments containing wet carbon dioxide gas of relatively low temperature, since the martensitic stainless steel has excellent resistance to carbon dioxide gas corrosion although it may not have sufficient resistance to sulfide stress corrosion cracking caused by hydrogen sulfide. Typical examples thereof include an oil well pipe of 13Cr type steel (having a Cr content of 12 to 14%) of L80 grade specified by API (American Petroleum Institute).
Generally, it is common to apply quenching and tempering treatments for the martensitic stainless steel, and the 13Cr steel of API L80 grade is no exception. However, since the 13Cr steel has a martensitic transformation starting temperature (Ms point) of about 300° C., which is lower than that of low alloy steel, and has a large hardenability, it exhibits high susceptibility to quench cracking.
Particularly, when a tubular steel product is quenched, it exhibits a very complex stress state, compared with the case of a sheet/plate or bar material, and when it is subjected to water cooling, quench cracking occurs; therefore, it is necessary to adopt a process with a slow cooling rate such as cooling in air (natural air cooling), forced air cooling, and slow mist cooling. For this reason, in the production of the 13Cr-type oil well pipe of L80 grade, air quenching is performed to prevent quench cracking. Since this type of alloy steel has a large hardenability, martensitization can be achieved even when the cooling rate at the time of the quenching treatment is slow.
However, although this method can be effective in preventing quench cracking, problems arise such that the productivity is low since the cooling rate is slow, and besides, various properties including the resistance to sulfide stress-corrosion cracking deteriorate.
In this way, even in a steel pipe of low alloy steel or medium alloy steel, or further in a martensitic stainless steel pipe, there is a problem of quench cracking in a quenching treatment, and thus there is a greater need for solving this problem particularly in a steel pipe, compared with a sheet/plate material and a bar material.
Conventionally, there have been proposed several techniques to solve such a quench cracking problem. For example, Patent Literature 1 discloses, as a method for preventing quench cracking of a steel pipe containing 0.2 to 1.2% of C, a method for quenching a steel pipe made of a medium or high carbon type of steel, in which cooling in a quenching process is performed only from an inner surface of the steel pipe, and whenever necessary, the steel pipe is rotated during cooling.
In the literature, it is suggested that: when the outer surface of the steel pipe is rapidly cooled, martensitic transformation of the outer surface precedes, and the brittle martensite structure of the outer surface cannot withstand the transformation stress due to a delayed martensitic transformation of the inner surface, thus leading to quench cracking; and it is possible to appropriately countervail the transformation stress and the thermal stress by cooling the steel pipe from the inner surface. However, there is a problem that performing the cooling of the inner surface of a steel pipe involves technical difficulties compared with the cooling of the outer surface.
Patent Literature 2 discloses, as a method for producing a steel pipe having a microstructure principally composed of martensite by applying quenching and tempering treatments for a Cr-based stainless steel pipe containing 0.1 to 0.3% of C and 11.0 to 15.0% of Cr, a method for producing a martensitic stainless steel pipe in which the steel pipe is quenched at an average cooling rate of not less than 8° C./sec in a temperature range from Ms point to Mf point (temperature at which martensitic transformation ends) when performing the quenching treatment, and thereafter the steel pipe is subjected to the tempering treatment. By ensuring the above-described cooling rate, it is possible to prevent the formation of retained austenite, thereby obtaining a microstructure principally composed of martensite.
However, in order to prevent quench cracking even in rapid cooling such as water quenching, the production method of Patent Literature 2 requires that cooling be performed only from the inner surface of a steel pipe, and further, as needed, the steel pipe be rotated, so that a problem similar to that of the quenching method according to Patent Literature 1 arises when put into commercial use.
Patent Literature 3 discloses a method for producing a martensitic stainless steel pipe, in which a stainless steel pipe containing 0.1 to 0.3% of C and 11 to 15% of Cr is quenched by performing a two-stage cooling to obtain a microstructure of which not less than 80% is martensite, and thereafter the stainless steel pipe is tempered, where the two-stage cooling consists of: a first cooling in which air cooling is performed from a quenching onset temperature until when the outer surface temperature becomes any temperature lower than “Ms point—30° C.” and higher than “an intermediate temperature between Ms point and Mf point”; and thereafter a second cooling in which rapid controlled cooling of the pipe outer surface is performed through a temperature range until the outer surface temperature becomes Mf point or lower, so as to ensure an average cooling rate of the pipe inner surface to be not less than 8° C./sec.
The method described in Patent Literature 3 is a method to prevent quench cracking by relatively reducing the cooling rate in the first cooling, and to suppress the formation of retained austenite by the rapid controlled cooling of the pipe outer surface in the second cooling. However, when the wall thickness is heavy, it is difficult to control the cooling rate of the pipe inner surface by cooling the outer surface.
Moreover, Patent Literature 4 discloses, as a method for producing a seamless steel pipe of low alloy steel containing a medium or high level of carbon of C: 0.30 to 0.60%, a method for performing water cooling down to a temperature range of 400 to 600° C. immediately after hot rolling, and after the end of water cooling, performing isothermal transformation heat treatment (austemper process) in a furnace heated to 400 to 600° C. However, the microstructure of the steel pipe which is produced by the isothermal transformation heat treatment according to Patent Literature 4 is bainite which generally has lower strength than martensite, and therefore it may not be able to cope with a case where a high strength is required.
As described above, when a medium or high carbon type of steel pipe (a steel pipe of low alloy steel or medium alloy steel) is quenched to obtain a high strength martensite structure, performing rapid cooling such as water quenching is likely to cause quench cracking. If a moderate cooling such as oil quenching is performed to avoid quench cracking, a sufficient amount of martensite structure cannot be obtained, thereby leading to degrade strength/toughness of the steel pipe.
Moreover, when producing a martensitic stainless steel pipe, although it is possible to obtain martensite structure even if the cooling rate is moderately slow at the time of a quenching treatment, the productivity is low due to the slower cooling rate, and various properties including resistance to sulfide stress-corrosion cracking deteriorate. If water quenching is performed to improve the productivity, quench cracking occurs.
The present invention has been made in view of the above-described problems, and has its object to provide a method for quenching a steel pipe which can be effective in preventing quench cracking in a medium or high carbon type of steel pipe (a steel pipe mostly of low alloy steel or medium alloy steel) or martensitic stainless steel.
The summaries of the present invention are as follows.
(1) A method for quenching a steel pipe by water cooling from an outer surface thereof, wherein pipe end portions avoid water cooling, and at least part of a main body other than the pipe end portions is subjected to water cooling.
(2) The method for quenching a steel pipe according to (1), wherein a region(s) that is not subjected to direct water cooling over an entire circumference thereof is provided along an axial direction at least in part of the main body other than the pipe end portions.
(3) The method for quenching a steel pipe according to (1) or (2), wherein the start and stop of water cooling are intermittently repeated at least in part of a quenching process.
(4) The method for quenching a steel pipe according to (1) or (2), wherein in order to perform water cooling for an outer surface of the steel pipe, an intensified water cooling is performed in a temperature range in which temperature of the outer surface of the steel pipe is higher than Ms point, thereafter switched to a moderate water cooling or air cooling to forcedly cool down the outer surface to Ms point or lower.
(5) The method for quenching a steel pipe according to any of (1) to (4), wherein the steel pipe contains 0.2 to 1.2% of C.
(6) The method for quenching a steel pipe according to any of (1) to (4), wherein the steel pipe is a Cr-based stainless steel pipe containing 0.10 to 0.30% of C and 11 to 18% of Cr.
According to the method for quenching a steel pipe of the present invention, it is possible to subject a medium or high carbon type of steel pipe (a steel pipe mostly of low alloy steel or medium alloy steel) or a Cr-based stainless steel pipe to a quenching treatment by use of rapid cooling means (water quenching) without causing quench cracking. This allows stable production of a high-strength steel pipe having a microstructure with a high martensite ratio (specifically, a martensite ratio being not less than 80%).
To solve the above-described problems, the present inventors have repeated experiments of water cooling in which steel-pipe test specimens made of low alloy steel containing a high level of carbon and Cr-based stainless steel were heated to not less than Ar3 transformation point temperature, and the steel pipe was subjected to water cooling from the outer surface. As a result of that, the following findings (a) to (f) have been obtained.
(a) When the entire steel pipe is cooled to not more than martensitic transformation finish temperature (Mf point) by an intensified water quenching, there is a high probability that quench cracking occurs.
(b) Since a crack at the time of quench cracking extends roughly in an axial direction of the steel pipe, it is inferred that primary stress to develop the crack is tensile stress in a circumferential direction.
(c) The cause of the generation of the tensile stress in a circumferential direction is possibly attributable to the lag of the timing of martensitic transformation between on the outer surface side and on the inner surface side because a temperature difference (temperature unevenness) along the wall thickness-wise direction occurs in the cooling procedure.
(d) Particularly in the vicinity of cooled surface where temperature unevenness is large (that is, temperature difference from the inner surface side is large), a microcrack due to brittle fracture is likely to occur, and this tends to be an initiation point of crack propagation.
(e) A fissure, in most cases, develops from an end portion of a steel pipe as the initiation point. This is presumably because a stress intensity factor at an end portion with a free surface is larger than that in any portion other than the end portions.
(f) When water cooling is not employed so as to suppress a cooling rate, quench cracking does not occur either in the case of low alloy steel containing a high level of carbon or Cr-based stainless steel. Note that in a low alloy steel containing a high level of carbon, martensitization is suppressed and a microstructure principally composed of bainite is obtained, so quench cracking does not occur.
In short, quench cracking is attributed in most cases to the consequence that a fissure generated at an end portion with a free surface of a steel pipe and acting as an initiation point of the crack is subjected to tensile stress (hereafter, “tensile stress” is also simply referred to as “stress”) in a circumferential direction due to thermal stress and transformation stress, the thermal stress being caused by temperature unevenness in a wall thickness-wise direction, the temperature unevenness occurring in the cooling procedure, and propagates via microcracks which occur in the vicinity of the cooled surface.
The present inventors further calculated the maximum stress generated in a circumferential direction of a steel pipe by an FEM (finite element method) analysis, taking thermal stress and transformation stress into account. In this FEM analysis, it is assumed that the steel pipe is uniformly cooled in an axial direction thereof, and a generalized plane strain model is applied to analyze a two-dimensional cross section of the steel pipe.
From the analysis result shown in
As being evident from
As so far described, the result of FEM analysis also revealed that it is possible to significantly reduce circumferential stress of the pipe end portions by applying air cooling for the pipe end portions, that is, no water cooling for them.
The present inventors have come up with the following ideas, (g) and (h), from the above-described findings and discussion, eventually completing the present invention:
(g) Even for a steel pipe made of a low alloy steel or medium alloy steel which is prone to occurrence of quench cracking in water quenching, it can be stably water quenched without causing quench cracking, provided that the end portions of the steel pipe are not subjected to water cooling, and the portions other than end portions of steel pipe are subjected to water cooling at a cooling rate which ensures a sufficient martensite ratio, and
(h) When the above-described water quenching method is applied to a steel pipe made of martensitic stainless steel, it is possible to ensure high performance without causing quench cracking.
As described so far, the present invention is a method for quenching a steel pipe by water cooling the steel pipe from the outer surface, in which pipe end portions are not subjected to water cooling, and at least part of a main body other than the pipe end portions is subjected to water cooling. It is to be noted that the “pipe end portions” refer to both end portions of a steel pipe.
The reason why the present invention is premised on that the steel pipe is quenched by the water cooling from the outer surface thereof is that compared with the inner surface cooling as described in the aforementioned Patent Literature 1 or 2, the outer surface cooling does not involve technical difficulties, and in the case where a Cr-based stainless steel pipe is a processing object, if it is possible to perform quenching by the water cooling from the outer surface without causing quench cracking, the productivity can significantly be improved.
In the following description, unless otherwise stated, cases of low alloy steel and medium alloy steel for which a certain cooling rate or more is needed for martensitization will be shown, regarding the metal microstructure to be formed.
In the present invention, as shown in
By adopting such cooling method, a steel micro-structure as shown in
In contrast to this, since a pipe end region (2), which is located on the side of the main body, out of the pipe end regions (2) and (3) in the end portion is adjacent to the main body (1) which is subjected to water cooling, the pipe end region (2) is cooled by conduction heat transfer, thereby undergoing martensitic transformation. However, since heat flows principally in an axial direction rather than in a circumferential direction, in the pipe end region (2), the temperature distribution in the wall thickness-wise direction is small compared with in the main body (1), and circumferential stress is low. As a result of that, the pipe end region (2) in the pipe end portion is not likely to cause fissure generation and extension even when martensitic transformation occurs. It is to be noted that since the profile/shape of the pipe end portion as rolled is not exactly cylindrical, it is usually desirable to cut off the pipe end portions by a length of about 150 to 400 mm at a subsequent processing stage. Thus, such pipe end portions which are principally composed of bainite and have a lower martensite ratio can be cut off and removed in a process after the quenching process.
The method for quenching a steel pipe of the present invention is a method of forming martensite structure of steel by quenching, in which the ratio of produced martensite is not specifically limited. However, in low alloy steel and medium alloy steel, generally, if not less than 80% of the structure is martensite, a desired strength can be obtained. When a product to be quenched is a Cr-based stainless steel pipe, although martensite is formed even when the cooling rate is moderately small, the quenching method of the present invention ensures desired corrosion resistance. In any case, the present invention intends to obtain a steel pipe having a martensite ratio of not less than 80%.
The present invention may adopt an embodiment in which a region(s) that is not subjected to direct water cooling over the entire circumference thereof is provided along an axial direction at least in part of a portion (main body of the pipe) other than pipe end portions.
This embodiment is particularly effective when, for example, the wall thickness of the steel pipe is thin. When the wall thickness of the steel pipe is thin, as shown in
In such a case, adopting the cooling method shown in
In the present invention, it is possible to adopt an embodiment in which in order to apply water cooling onto the outer surface of the steel pipe, the start and stop of water cooling are intermittently repeated during at least in part of the quenching process. By adopting an intermittent water cooling scheme, the total water cooling time increases compared with continuous water cooling, and thereby the difference between the inner temperature and the surface temperature decreases, resulting in a decrease in residual stress.
In the present embodiment, it is possible to consistently perform the intermittent water cooling from the initial stage of a quenching treatment in which the temperature of the steel pipe is not less than Ar3 point until the temperature of the inner and outer surfaces of the steel pipe becomes not more than Ms point, preferably not more than Mf point, and also to use it as part of the quenching process.
The present invention may adopt an embodiment in which in order to apply water cooling onto the outer surface of the steel pipe, an intensified water cooling is performed in a temperature range in which the temperature of the outer surface of the steel pipe is higher than Ms point, thereafter switched to a moderate water cooling or air cooling (including forced air cooling), and after the temperature difference between those of the outer surface of the steel pipe and the inner surface of the steel pipe is decreased, the outer surface is forcedly cooled down to not more than Ms point.
In the cooling method describe above in which the intensified water cooling is switched to the moderate water cooling or air cooling, it is desirable that the intensified water cooling to a temperature near but higher than Ms point is performed, thereafter switched to the moderate water cooling or air cooling; heat recovery is caused to occur in the outer surface side of the steel pipe through thermal conduction from the inner surface side so as to decrease the temperature difference between the inner and outer surfaces of the steel pipe as much as possible; and thereafter cooling to not more than Ms point, preferably not more than Mf point is performed by forced air cooling, etc.
This embodiment is particularly effective, for example, when the wall thickness of the steel pipe is heavy. When the wall thickness of the steel pipe is heavy, temperature unevenness in the wall thickness-wise direction may increase during the water cooling from the outer surface, and brittle fracture may occur which is an initiation point of a crack in the outer surface caused by a large tensile stress due to expansion associated with martensitic transformation in the outer surface. To suppress this, the embodiment is effective in which the start of the martensitic transformation in the outer surface is delayed to reduce the difference between the starting time of martensitic transformation in the inner surface and that in the outer surface.
By the embodiment, it is possible to mitigate the temperature gradient in the wall thickness-wise direction, thereby reducing the tensile stress which occurs in a circumferential direction. Particularly, it is desirable that the temperature difference between the inner and outer surfaces is mitigated before the temperature of the cooled outer surface passes Ms point. In practice, it is desirable to monitor the temperature of the water cooled portion of the outer surface of the steel pipe, and stop the water cooling before the temperature passes Ms point.
As for the cooling rate for an intensified water cooling, although it depends on types of steel, it is desirable to determine an appropriate cooling rate based on a CCT diagram of the target steel, since in the case of a low alloy steel, when the cooling rate in the initial cooling stage is too slow, bainite transformation occurs and it becomes impossible to ensure a sufficient martensite ratio.
It is to be noted that in the embodiment of the present invention, which includes a cooling process in which an intensified water cooling is performed down to a temperature near but higher than Ms point, thereafter switched to a moderate cooling or air cooling, and heat recovery is caused to occur in the outer surface side of the steel pipe through thermal conduction from the inner surface side so as to decrease the temperature difference between the inner and outer surfaces of the steel pipe as much as possible, it is also possible to achieve similar effects by using, instead of this cooling process, the previously-described intermittent cooling.
That is, in the present invention, the intermittent water cooling (operation to intermittently repeat the start and stop of water cooling) according to the present invention (3) may also be suspended at a temperature near but higher than Ms point, and thereafter an intensified cooling such as forced air cooling may be performed. However, this embodiment belongs to the category of the present invention (3).
In the method for quenching a steel pipe of the present invention described so far, as the scheme of water cooling, conventionally used schemes such as laminar cooling, jet cooling, mist cooling, and the like may be appropriately adopted. On top of that, it is desirable to make temperature deviation in the wall thickness-wise direction smaller by increasing/decreasing the amount of water during water cooling, or intermittently repeating the start and stop of water cooling, thereby reducing the circumferential stress of the steel pipe. It is desirable that the inside of steel pipe is naturally cooled in the air or forcedly air cooled instead of water cooling. Moreover, it is desirable to keep rotating the steel pipe during water cooling since thereby the temperature distribution in the circumferential direction can be made uniform.
The product to be processed by the present invention is a steel pipe which is likely to cause quench cracking at the time of a quenching treatment. In particular, the effect of the present invention is remarkably exhibited when the product to be processed by the present invention is (A) a steel pipe containing 0.20 to 1.20% of C, and among others, a steel pipe of low alloy steel or medium alloy steel, or (B) a Cr-based stainless steel pipe containing 0.10 to 0.30% of C and 11 to 18% of Cr, and among others a 13Cr stainless steel pipe.
The steel pipe of the above-described (A) containing 0.20 to 1.20% of C is a steel pipe made of a material in which C is contained in this range, and is generally a steel pipe of low alloy steel or medium alloy steel. When the content of C is less than 0.20%, quench cracking hardly becomes a problem since the volume expansion due to martensitization is relatively small.
On the other hand, when C is more than 1.20%, Ms point becomes lower, and retained austenite is likely to occur so that obtaining a microstructure having a martensite percentage of not less than 80% becomes difficult. Therefore, a C content of 0.20 to 1.20% is desirable so that the present invention exhibits its effects. The C content is more desirably 0.25 to 1.00%, and furthermore desirably 0.3 to 0.65%.
In a steel pipe of low alloy steel or medium alloy steel containing 0.20 to 1.20% of C, as shown in
Examples of low alloy steel or medium alloy steel include, for example, a steel consisting of C: 0.20 to 1.20%, Si: 2.0% or less, Mn: 0.01 to 2.0%, and one or more elements selected from a group consisting of Cr: 7.0% or less, Mo: 2.0% or less, Ni: 2.0% or less, Al: 0.001 to 0.1%, N: 0.1% or less, Nb: 0.5% or less, Ti: 0.5% or less, V: 0.8% or less, Cu: 2.0% or less, Zr: 0.5% or less, Ca: 0.01% or less, Mg: 0.01% or less, B: 0.01% or less, the balance being Fe and impurities, the impurities being P: 0.04% or less and S: 0.02% or less. It is to be noted that when the Cr content is more than 7.0%, martensite is likely to be formed even in the pipe end portions which are not subjected to water cooling, and therefore the Cr content is desirably not more than 7.0%.
Next, the Cr-based stainless steel pipe of the above-described (B) containing 0.10 to 0.30% of C and 11 to 18% of Cr is a steel pipe (martensitic stainless steel pipe) made of Cr-based stainless steel in which C and Cr are contained in this range. When the content of C is less than 0.10%, it is not possible to achieve sufficient strength even if quenching is performed, and on the other hand, when C is more than 0.30%, it is unavoidable that the austenite is retained, and it becomes difficult to ensure a martensite ratio of not less than 80%. Therefore, the C content of 0.10 to 0.30% is desirable so that the present invention exhibits its effects.
The reason why the content of Cr is 11 to 18% is that in order to improve corrosion resistance, Cr of 11% or more is desirable, and on the other hand, when Cr is more than 18%, δ-ferrite is likely to be generated, thereby reducing hot workability. More desirably, Cr is 10.5 to 16.5%.
Examples of Cr-based stainless steel containing 0.10 to 0.30% of C and 11 to 18% of Cr include, for example, a steel consisting of C: 0.10 to 0.30%, Si: 1.0% or less, Mn: 0.01 to 1.0%, Cr: 11 to 18% (more desirably, 10.5 to 16.5%), and one or more elements selected from a group consisting of Mo: 2.0% or less, Ni: 1.0% or less, Al: 0.001 to 0.1%, N: 0.1% or less, Nb: 0.5% or less, Ti: 0.5% or less, V: 0.8% or less, Cu: 2.0% or less, Zr: 0.5% or less, Ca: 0.01% or less, Mg: 0.01% or less, B: 0.01% or less, the balance being Fe and impurities, the impurities being P: 0.04% or less and S: 0.02% or less. Among others, 13Cr stainless steel pipes are conventionally used in many industrial areas and are suitable as the object to be processed by the present invention.
The quenching method of the present invention is applicable, as a matter of course, to so-called quenching accompanied by reheating, which is performed by reheating a steel pipe from ambient temperature, as well as to so-called direct quenching in which a steel pipe immediately after hot rolling is quenched from a state where the temperature of the steel pipe is not less than Ar3 point during the production of a seamless steel pipe, and further to a quenching method for so-called inline heat treatment (inline quenching) in which the steel pipe is soaked (complementarily heated) at a temperature not less than A3 point in a stage in which the heat retained by the steel pipe is not significantly decreased after hot rolling, and is thereafter quenched. Since according to the quenching method of the present invention, quench cracking can be effectively prevented, it is possible to stably produce a high-strength steel pipe having a microstructure with a high martensite ratio.
A tubular test material was cut out from a seamless steel pipe of the material shown in Table 1, and quenched under various cooling conditions to observe the presence or absence of quench cracking, and steel micro-structure. In Table 1, steel type A is a low alloy steel, and steel type B is a high Cr steel (martensitic stainless steel).
The configuration of the test material was a straight pipe having an outer diameter of 114 mm, a wall thickness of 15 mm, and a length of 300 mm. This test material was heated to a temperature about 50° C. higher than the Ac3 point by an electric heating furnace, held for about 15 minutes, and thereafter carried from the furnace to be conveyed to a cooling apparatus within 30 seconds to start water cooling.
Table 2 shows water cooling conditions. In Table 2, at water cooling condition A, the inner surface temperature of a main body of the steel pipe was measured by a thermocouple adhered by welding to the inner wall of the steel pipe. Moreover, at water cooling conditions B to E, the outer surface temperature of the main body of steel pipe, or the main body of steel pipe and both left and right end portions of the steel pipe was measured by a thermotracer.
Table 3 shows the observation results of the presence or absence of quench cracking and steel micro-structure.
The reason for this is considered to be that in the main body of the steel pipe, martensitization progressed in a state in which the temperature difference between the inner and outer surfaces was mitigated as a result of intensified water cooling followed by moderate water cooling being performed in a temperature range higher than Ms point, and in the pipe end portions, bainite was formed because water cooling was not performed, so that occurrence of a fissure which acts as an initiation point of quench cracking was suppressed. While the formation of bainite in the pipe end portions were recognizable due to a temporary temperature rise possibly caused by bainitic transformation at around 400° C. shown in
It is to be noted that from
Although a description has been provided so far regarding the case in which the steel pipe of steel type A was cooled, in the case in which a steel pipe of steel type B (high Cr steel) was cooled, the micro-structure was composed of martensite of not less than 90% in volume ratio under any of the water cooling conditions of Test Nos. 1 to 5 as shown in Table 3. However, in Test Nos. 1 and 2 in which the entire steel pipe was subjected to water cooling, quench cracking occurred since rapid martensitization occurred even in the pipe end portions.
It is to be noted that since the steel type B was a material capable of martensitization even by slow cooling, heat generation around 400° C. (see
From the test results described so far, it can be confirmed that a microstructure principally composed of martensite can be obtained without occurrence of quench cracking by applying the method for quenching a steel pipe of the present invention.
Since the method for quenching a steel pipe of the present invention will not cause quench cracking even when applied to a steel pipe made of a medium or high carbon type of steel (a steel pipe of low alloy steel or medium alloy steel) or a Cr-based stainless steel pipe, which is likely to cause quench cracking, it can be suitably utilized for the quenching treatment of those steel pipes.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-060726 | Mar 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/001708 | 3/13/2012 | WO | 00 | 9/18/2013 |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2012/127811 | 9/27/2012 | WO | A |
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| 101962707 | Feb 2011 | CN |
| 62-63618 | Mar 1987 | JP |
| 8-188827 | Jul 1996 | JP |
| 9-104925 | Apr 1997 | JP |
| 10-17934 | Jan 1998 | JP |
| 11-080833 | Mar 1999 | JP |
| 11-229037 | Aug 1999 | JP |
| 2005-036308 | Feb 2005 | JP |
| 2006-213933 | Aug 2006 | JP |
| 2006-265657 | Oct 2006 | JP |
| 100930733 | Dec 2009 | KR |
| 1754791 | Aug 1992 | SU |
| Entry |
|---|
| Partial Translation of JP S62-63618 A, Ishimoto et al. (Mar. 1987). |
| Classification and Designation of Carbon and Low-Alloy Steels, Properties and Selection: Irons, Steels, and High-Performance Alloys, vol. 1, ASM Handbook, ASM International, 1990, p , no author 140-194. |
| Full English Translation of JP S62-63618 A, Ishimito et al. (Mar. 1987). |
| Number | Date | Country | |
|---|---|---|---|
| 20140007994 A1 | Jan 2014 | US |
