JP2009114471A - High strength stainless steel pipe - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a high strength stainless steel pipe with which the strength and the corrosion resistance are good and the pipe can be manufactured at low cost. <P>SOLUTION: A stainless steel material having the component composition composed, by mass, of 0.04-0.12% C, 0 (non-addition)-5.0% Ni, 12.0-17.0% Cr, 0 (non-addition)-0.10% N, 0.2-2.0% Si, ≤2.0% Mn, 0 (non-addition)-2.0% Cu, ≤0.06% P, ≤0.006% S and the balance Fe with inevitable impurities, is used as a basic material. Further, a basic phase is constituted of any structure of a single phase structure of a ferrite phase or a martensite phase , or a dual phase structure of the ferrite phase and the martensite phase. The end edge part of the basic material is melt-welded as a joining part to make the pipe. In the basic phase, carbide is uniformly precipitated at a crystal grain boundary and in the crystal grain, and solid-solution C content is ≤0.03 mass%. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

  The present invention relates to a high-strength stainless steel pipe that is used for transportation, machine structure, building, decoration, and the like, and particularly suitable for applications requiring strength and corrosion resistance.

  Stainless steel materials are excellent in corrosion resistance and have good strength, workability, joint properties, etc., so stainless steel pipes made from such stainless steel materials can be used in various applications in terms of high corrosion resistance and high strength. used.

  Furthermore, in recent years, cost reduction is also required, and the high-strength stainless steel pipe used is required to improve corrosion resistance and strength without containing expensive elements.

  And by mass%, based on 12% Cr martensitic stainless steel material, the Cr content is increased, the C and N content is reduced, and the proper amount of Cr, Ni, Mo, Cu is further contained. The strength, hot workability, corrosion resistance, and weldability are improved by adopting a multiphase structure formed from the ferrite phase and the retained austenite phase with the martensite phase as the base phase. (For example, refer to Patent Document 1).

  Moreover, after reducing the N content to 0.015% or less by mass%, welding a martensitic stainless steel material to form a stainless steel pipe, austenitizing at 920 to 1100 ° C., cooling beyond water cooling There are high-strength stainless steel pipes that have martensite produced by cooling at a speed, tempering, and cooling at a cooling speed higher than air cooling. This high-strength stainless steel pipe has sufficient corrosion resistance even in a carbon dioxide environment, and has excellent impact toughness and weldability (see, for example, Patent Document 2).

  Furthermore, with regard to the metal structure, workability and corrosion resistance are improved by introducing an appropriate amount of ferrite phase into the austenite matrix and making it into an austenite-based two-phase structure containing 5 to 40% ferrite phase in volume%. (For example, refer to Patent Document 3).

Moreover, by combining Mo and V into ferritic stainless steel material and containing appropriate amounts, the corrosion resistance is improved, and further, by controlling the hot rolling conditions and the cold rolling conditions, the workability due to the inclusion of Mo is improved. Some have suppressed the decrease (see, for example, Patent Document 4).
Japanese Patent Laying-Open No. 2005-336599 (page 2-7, FIG. 1) JP-A-4-268018 (pages 2 and 3) Japanese Patent Laying-Open No. 2004-225075 (pages 2, 3 and 1) Japanese Patent Laid-Open No. 2002-363712 (pages 2, 3 and 1)

  However, in the stainless steel material of Patent Document 1, it is preferable that the tensile strength is 689 MPa or less and the strength is further improved. Further, since Mo, which is a relatively expensive element, is contained, the cost increases. There is.

  In addition, the stainless steel material of Patent Document 2 has good corrosion resistance and impact toughness, but it is preferable to further improve the strength, and furthermore, since Co, which is a relatively expensive element, is contained, the cost increases. There is a problem.

  The stainless steel materials of Patent Document 3 and Patent Document 4 are piped in the state after the final annealing and are used without being subjected to heat treatment after the pipe making, so that the workability is good, but high strength cannot be obtained. There's a problem.

  The present invention has been made in view of these points, and provides a high-strength stainless steel pipe that has good strength and corrosion resistance and can be manufactured at low cost.

  The invention described in claim 1 is mass%, C: 0.04 to 0.12%, Ni: 0 (including no addition) to 5.0%, Cr: 12.0 to 17.0% N: 0 (including no addition) to 0.10%, Si: 0.2 to 2.0%, Mn: 2.0% or less, Cu: 0 (including no addition) to 2.0%, P: 0.06% or less, S: 0.006% or less, the balance being Fe and inevitable impurities, the parent phase is a single phase structure of ferrite phase, single phase structure of martensite phase, ferrite phase and martens A stainless steel material composed of one of the multiphase structures of the site phase is used as a base material, and the base phase is formed by melting and welding using an end portion of the base material as a joint portion. In the grain boundaries and crystal grains, carbides are uniformly precipitated and the amount of solute C is adjusted to 0.03% or less. Parts is a high strength stainless steel pipe having a melt tissue by fusion welding.

  According to a second aspect of the present invention, in the high-strength stainless steel pipe according to the first aspect, the matrix and the joint are formed by dissolving precipitated carbides by heat treatment after pipe forming.

  The invention described in claim 3 is the high-strength stainless steel pipe described in claim 2, wherein the parent phase and the joint after heat treatment are a single phase structure of martensite phase or a double phase of martensite phase and ferrite phase. It consists of an organization.

  According to the invention described in claim 1, the composition of the stainless steel material is defined, and the parent phase of the stainless steel material is a single phase structure of a ferrite phase, a single phase structure of a martensite phase, a multiphase structure of a ferrite phase and a martensite phase. By being comprised by either, after a pipe making, a parent phase turns into the structure | tissue containing the martensite phase and can improve intensity | strength.

  Moreover, since the component composition is comprised only with the element used for a normal stainless steel material, it can manufacture inexpensively.

  In stainless steel materials, carbides precipitate uniformly in the grain boundaries of the parent phase and within the crystal grains, resulting in reduced workability during pipe making due to local precipitation of carbides at the crystal grain boundaries and reduced toughness. Can be prevented. Moreover, it can prevent that the amount of solid solution Cr reduces and corrosion resistance falls by local precipitation of the carbide | carbonized_material in a crystal grain boundary.

  By adjusting the solid solution C amount of the mother phase to 0.03% by mass or less, it is possible to prevent an increase in processing load during pipe making and generation of surface processing defects due to excessively high strength. Moreover, the carbide | carbonized_material which precipitates by the increase in the amount of solid solution C increases, In order to form this carbide | carbonized_material which precipitates, it can prevent that the amount of solid solution Cr reduces and corrosion resistance falls.

  According to the second aspect of the present invention, the carbide precipitated in the mother phase and the joint is dissolved in the mother phase and the joint by the heat treatment after pipe forming. Strength and corrosion resistance can be improved. In addition, at the time of pipe making before heat treatment, it is in a state where carbides are deposited, so that it can be easily formed.

  According to the invention described in claim 3, the parent phase and the joint portion after pipe forming and heat treatment are a single phase structure of martensite phase or a multiphase structure of martensite phase and ferrite phase, The strength of the mother phase and the joint can be improved. In the case of a multiphase structure of martensite phase and ferrite phase, the higher the volume ratio of the martensite phase, the higher the strength.

  Hereinafter, embodiments of the present invention will be described in detail.

  Each element of the stainless steel material that is the base material of the high-strength stainless steel pipe of this embodiment and the content of each element will be described. The content of each element is mass% unless otherwise specified.

[C: 0.04 to 0.12%]
C is an element that improves the strength, and in particular, is an important element that improves the strength by forming a solid solution in the parent phase and the joint by heat treatment after pipe forming. In order to obtain an effective strength as stainless steel constituting the base material of the high-strength stainless steel pipe, it is necessary to contain 0.04% or more. However, as the C content increases, the amount of Cr that forms carbides with C also increases. For this reason, the amount of solid solution Cr decreases, and corrosion resistance will fall. Furthermore, if the C content exceeds 0.12%, the amount of carbide is excessively increased, ductility and toughness are lowered, and workability at the time of pipe making is deteriorated. Therefore, the C content is 0.04 to 0.12%.

[Ni: 0 to 5.0%]
Ni is an element that can prevent a decrease in corrosion resistance due to the excessive content of C and N by substituting part of C and N. However, if the Ni content exceeds 5.0%, the strength decreases due to an increase in the amount of retained austenite. Therefore, the upper limit of the Ni content is 5.0%. In addition, by adjusting the content of Cr, which is a ferrite-forming element, and the contents of C, N, which are austenite-generating elements, the parent phase of the stainless steel material is a single-phase structure of a ferrite phase, a single-phase structure of a martensite phase, Since it can be constituted by either a ferrite phase or a multiphase structure of a martensite phase, Ni is not necessarily contained.

[Cr: 12.0 to 17.0%]
Cr is an element that improves the corrosion resistance of the parent phase and the joint. In order to obtain effective corrosion resistance as the stainless steel constituting the base material of the high-strength stainless steel pipe, it is necessary to contain 12.0% or more. . However, if the Cr content exceeds 17.0%, it becomes difficult to obtain a martensite phase by heat treatment after pipe forming. Further, even if the component is adjusted by the inclusion of the austenite-forming element, the strength of the parent phase and the joint portion is reduced due to the increase of retained austenite. Therefore, the Cr content is 12.0 to 17.0% [N: 0 to 0.10%]
N, like C, is an element that improves the strength. In particular, N can be dissolved in the parent phase by heat treatment after pipe forming, and the strength can be improved. Moreover, since a part of C can be substituted with N, ductility and toughness are prevented from being lowered due to a large amount of C. However, when the N content exceeds 0.10%, the strength is lowered due to an increase in retained austenite. Accordingly, the upper limit of the N content is 0.10%. Note that N is not necessarily contained.

[Si: 0.2-2.0%]
Si is an element that improves the strength of the matrix phase by solid solution strengthening. In order to obtain an effective strength as a stainless steel constituting the base material of the high-strength stainless steel pipe, it is necessary to contain 0.2% or more. However, if the Si content exceeds 3.0%, the solid solution strengthening action is saturated, and the formation of the δ ferrite phase is promoted to reduce ductility and toughness. Therefore, the Si content is set to 0.2 to 2.0%.

[Mn: 2.0% or less]
Mn suppresses the formation of a β ferrite phase in a high temperature range. Further, it supplements S as MnS and has the effect of improving manufacturability. However, the inclusion of a large amount of Mn increases the amount of retained austenite after annealing and causes a decrease in strength. For this reason, the upper limit of the Mn content is 2.0%. In addition, it is preferable that content of Mn is 0.1 to 1.2%.

[Cu: 0 to 2.0%]
Cu is an element effective in suppressing the formation of a β ferrite phase in a high temperature range and improving the corrosion resistance. However, if the Cu content exceeds 2.0%, residual austenite or β-ferrite is generated in the parent phase or welded part, which causes a decrease in strength. Therefore, the upper limit of the Cu content is 2.0%. Note that Cu is not necessarily contained.

[P: 0.06% or less]
P is an element that causes a decrease in corrosion resistance. Accordingly, the smaller the P content, the better. However, if the P content is extremely reduced, the production cost increases. Therefore, the upper limit of the P content is set to 0.06 as a range that does not substantially adversely affect the P content. %.

[S: 0.006% or less]
S is an element that segregates at the grain boundaries during hot rolling to reduce hot workability and causes hot working cracks, rough skin, and the like, and also causes ear cutting in cold rolling after intermediate annealing. . In addition, when a large amount of MnS is present, the corrosion resistance is adversely affected. Accordingly, the smaller the S content, the better. However, if the S content is extremely reduced, the manufacturing cost increases. Therefore, the upper limit of the S content is set to 0.006 as a range that does not substantially adversely affect the production cost. %.

  Moreover, in addition to the element mentioned above as needed, you may contain 3.0% or less of Mo, 0.01% or less of B, and 0.5% or less of Nb, Ti, and V.

[Mo: 3.0% or less]
Mo is an element that improves the corrosion resistance. However, if the Mo content exceeds 3.0%, the hot workability is lowered. Moreover, since it is a comparatively expensive element, when it contains abundantly, cost will become high. Therefore, the upper limit of the Mo content is 3.0%.

[B: 0.01% or less]
B is an element that improves the hot workability by forming fine precipitates to suppress coarsening of the grains and increasing the bond strength at the grain boundary between the ferrite phase and the austenite phase in the hot rolling temperature range. It is. However, if the B content exceeds 0.01%, formation of a low-melting boride is caused and hot workability is deteriorated. For this reason, the upper limit of the B content is 0.01%.

[Nb, Ti, V: 0.5% or less]
Nb, Ti, and V are elements that refine crystal grains and further generate precipitates to improve strength. However, if the content of each of Nb, Ti, and V exceeds 0.5%, the toughness decreases due to the formation of intermetallic compounds. Therefore, the upper limit of each Nb, Ti, and V content is 0.5%.

  The balance other than the above-mentioned elements is composed of Fe and inevitable impurities. By adjusting the composition of the components in this way, the parent phase is a single phase structure of a ferrite phase, a single phase structure of a martensite phase, a ferrite phase and a martensite. It becomes a stainless steel material composed of one of the multiphase structures of the site phase.

  Stainless steel is heat treated twice before pipe making, so that carbides are uniformly deposited in the grain boundaries and crystal grains of the parent phase, and the amount of dissolved C is adjusted to 0.03% by mass or less. Has been.

  The carbide is formed by combining C and one or more other elements, and also includes carbonitride in which C, N, and other elements are combined.

  In addition, the state in which carbides are uniformly precipitated in the crystal grain boundaries and in the crystal grains is a deviation in the area ratio of carbides depending on the observation location in a 1 μm square field observed at a magnification of 100,000 times using a transmission electron microscope. Is 80% or less. Note that a state where carbides are continuously precipitated in the crystal grain boundary or in the crystal grain is excluded.

  First, the stainless steel material is subjected to a first heat treatment at a material temperature of 600 to 850 ° C. and a soaking time of 0 to 24 h, whereby solid solution C is precipitated as substantially the entire amount of carbide.

  Here, the carbide is likely to precipitate at the crystal grain boundary from within the crystal grain, and the carbide is preferentially precipitated at the crystal grain boundary after the first heat treatment. In the state where carbides are preferentially precipitated at the grain boundaries, the toughness decreases and the workability deteriorates. In addition, since the precipitated carbide includes chromium carbide formed by combining C and Cr, when the carbide is locally preferentially precipitated at the crystal grain boundary, the amount of solid solution Cr due to the formation of local carbide. Decreases and a Cr-deficient layer is formed.

  Note that the Cr-deficient layer is a region in which the Cr content is 2% by mass or more lower than the Cr content of the parent phase due to, for example, formation of chromium carbide, and the corrosion resistance deteriorates.

  Furthermore, after descaling, cold rolling is performed at a rolling rate of 20% or more, and cold strain is introduced.

  Then, the second heat treatment is performed with a temperature difference of 50 ° C. or less from the first heat treatment temperature and a soaking time of 0 to 1 h. By this second heat treatment, the carbide is uniformly precipitated in the crystal grain boundaries and crystal grains of the parent phase.

  Further, the solid solution C amount of the parent phase is adjusted to 0.03% by mass or less by the second heat treatment. The greater the amount of solute C, the higher the strength of the stainless steel material. When the amount of solute C exceeds 0.03% by mass, the strength becomes excessively high and the processing load during pipe making increases, and the workability increases. It deteriorates and surface flaws are easily generated. Furthermore, during the cooling process during pipe forming, solid solution C in the joint forms carbide and precipitates, so if the amount of solid solution C exceeds 0.03% by mass, chromium carbide, which is one of the carbides, is formed. The amount of Cr to be increased increases excessively, and a Cr-deficient layer is easily formed. Accordingly, the upper limit of the amount of solid solution C is 0.03% by mass.

  Thus, in the stainless steel material, from the viewpoint of toughness, corrosion resistance, and workability at the time of pipe forming, carbides are uniformly precipitated in the crystal grain boundaries and crystal grains of the parent phase, and the amount of solute C is 0.03% by mass or less. In addition, it is desirable that the Cr deficient layer does not exist.

  In addition, the stainless steel material constituting the base material of the high-strength stainless steel pipe is such that carbides are uniformly precipitated in the crystal grain boundaries and crystal grains of the parent phase, and the solid solution C content of the parent phase is adjusted to 0.03% by mass or less. As long as the heat treatment is performed, the heat treatment is not limited to the first heat treatment, the cold rolling, and the second heat treatment. For example, heat treatment under different conditions may be performed.

  And the end part of such a base material is used as a joint part, and is welded by, for example, fusion welding such as TIG welding, MIG welding, high-frequency welding, etc. to produce a pipe.

  In the joint after pipe forming, a molten structure different from the parent phase is formed by fusion welding.

  The formed stainless steel pipe is heat-treated at a material temperature of 950 to 1100 ° C. and a soaking time of 0 to 1 h, and the carbide precipitated in the mother phase and the joint is dissolved, and the mother phase and the joint are carbide. Is in a solid solution state.

  In this way, the carbide precipitated in the parent phase and the joint is dissolved in the parent phase and the joint by heat treatment after pipe forming, thereby improving the strength and corrosion resistance of the parent phase and the joint of the high-strength stainless steel pipe. It is preferable because it is possible.

  In addition, the method of dissolving the precipitated carbide in the matrix and the joint is not limited to the above-described heat treatment, and may be a heat treatment under different conditions, for example.

  Forming and heat-treating a stainless steel material in which the parent phase before pipe formation is composed of either a single phase structure of a ferrite phase, a single phase structure of a martensite phase, or a double phase structure of a ferrite phase and a martensite phase As a result, the parent phase and the joined portion of the stainless steel pipe have a structure containing a martensite phase.

  Thus, when the structure constituting the parent phase and the joint after the heat treatment is a single phase structure of the martensite phase or a multiphase structure of the martensite phase and the ferrite phase, the strength of the mother phase and the joint is good. This is preferable.

  In the case of a multiphase structure of a martensite phase and a ferrite phase, the higher the volume ratio of the martensite phase, the more the strength is improved, and the volume ratio of the martensite phase is preferably 30% by volume or more.

  In addition, the content of some retained austenite does not adversely affect the strength of the high-strength stainless steel pipe, but the volume ratio of the austenite phase is preferably 20% by volume or less.

  Next, the operation and effect of the above embodiment will be described.

  When manufacturing high-strength stainless steel pipes, the parent phase is composed of a single phase structure of ferrite phase, a single phase structure of martensite phase, a multiphase structure of ferrite phase and martensite phase, with a specified component composition. A stainless steel material is used as a base material.

  Such a base material is subjected to a heat treatment at a material temperature of 600 to 850 ° C. and a soaking time of 0 to 24 h as a first heat treatment, and after descaling, cold rolling is performed at a cold rolling rate of 20% or more to obtain a cold strain. Is introduced. Furthermore, as a second heat treatment, by performing heat treatment at a temperature difference of 50 ° C. or less from the first heat treatment temperature and a soaking time of 0 to 1 h, the carbides in the crystal grain boundaries and crystal grains of the parent phase The amount of solid solution C in the matrix is adjusted to 0.03% by mass or less.

  Further, the end portion of the base material is used as a joint, and the pipe is formed by, for example, fusion welding such as TIG welding, MIG welding, and high-frequency welding, and a molten structure different from the parent phase is formed in the joint.

  And after pipe making, by carrying out heat treatment at a material temperature of 950 to 1100 ° C. and a soaking time of 0 to 1 h, carbides precipitated in the mother phase and the joint are dissolved in the mother phase and the joint, and high strength A stainless steel pipe is formed.

  The parent phase of the stainless steel material is composed of a single phase structure of the ferrite phase, a single phase structure of the martensite phase, and a double phase structure of the ferrite phase and the martensite phase. Since the structure includes a martensite phase, the strength of the parent phase and the joint can be improved.

  Here, for example, if the austenite phase is contained in the parent phase of the stainless steel material, the austenite phase tends to remain after pipe forming, and if a large amount of this austenite phase remains, it is difficult to improve the strength.

  The stainless steel material is heat-treated twice, and the carbides are uniformly precipitated in the crystal grain boundaries and crystal grains of the parent phase, so that the carbides are preferentially precipitated locally at the crystal grain boundaries and the toughness of the parent phase is lowered. Therefore, it is possible to prevent deterioration of workability during pipes.

  In addition, by adjusting the solid solution C amount of the matrix to 0.03% by mass or less by two heat treatments, the strength of the stainless steel material becomes excessively high due to the increase of the solid solution C amount, and the workability is increased. It is possible to prevent an increase in the processing load during pipe making due to the deterioration of steel and the generation of processing flaws on the surface of the stainless steel material. Moreover, the carbide | carbonized_material which precipitates by the increase in the amount of solid solution C increases, and since it forms the carbide | carbonized_material which precipitates, it can prevent that the amount of solid solution Cr reduces and corrosion resistance falls.

  Furthermore, carbides are uniformly precipitated in the crystal grain boundaries and crystal grains of the parent phase, and the amount of solid solution C in the parent phase is adjusted to 0.03% by mass, so that the carbides are given priority over the crystal grain boundaries. Formation of a Cr-deficient layer due to precipitation and formation of a Cr-deficient layer due to local precipitation of carbides at the joint in the cooling step during pipe making can be prevented.

  By preventing the formation of the Cr-deficient layer, it is possible to prevent a decrease in corrosion resistance, to prevent the occurrence of the mother phase, and to prevent the possibility of impairing the surface quality.

  By forming a molten structure by fusion welding, the joint portion can be reliably joined to each other and can be reliably piped.

  In the parent phase and the joint portion, the precipitated carbide is solid-dissolved by the heat treatment after pipe forming. Therefore, after the pipe forming, C is in a solid solution state in the mother phase and the joint portion. Strength and corrosion resistance can be improved. In addition, since the carbide is not in solid solution in the parent phase and the joined portion before the heat treatment, the workability is good and the tube is easily formed.

  Furthermore, since the carbide is solid-dissolved in the parent phase and the joint by heat treatment after pipe forming, variation in hardness between the parent phase and the joint can be suppressed, and the dimensional accuracy by processing can be improved.

  The strength of the parent phase and the joint can be improved by forming the parent phase and the joint after pipe forming and heat treatment with a single phase structure of the martensite phase or a multiphase structure of the martensite phase and the ferrite phase.

  In addition, the high-strength stainless steel pipe formed in this way can constitute the component composition with elements used in ordinary stainless steel materials without using expensive elements, and further, ordinary stainless steel pipes without special treatment Can be manufactured at a low cost.

  Table 1 shows the composition of the stainless steel materials as the present examples, comparative examples, and conventional examples.

  Steel type numbers A to C are stainless steel materials formed with the specified component composition, and are in this example. Steel type number D is a comparative example in which the C content is less than the defined component composition. Further, the steel type number E is SUS430LX of the conventional example, and the steel type number F is SUS304 of the conventional example.

  About the stainless steel material of the component composition shown by Table 1, the rolled plate of plate thickness 3.0mm was created through the hot rolling from the steel ingot of 100 kg, respectively.

  And these rolled plates were built in the process shown by Table 2, and it was set as the stainless steel plate of plate thickness 1.0mm.

  Furthermore, in these stainless steel materials, the amount of dissolved C was measured, and the metal structure and the precipitation state of carbides were confirmed.

The amount of solid solution C was measured by analyzing the extraction residue. The extraction residue was collected using a 10 mass% C ₅ H ₈ O ₂ (acetylacetone) +1 mass% (CH ₃ ) ₄ N ⁺ CL ⁻ (tetramethylammonium chloride) + CH ₃ OH (methanol) solution with a dissolution voltage of 40. Performed at ~ 70 mV. And about the extract | collected residue, C content in a residue was calculated | required by performing weight analysis and quantitative analysis of EPMA (X-ray microanalyzer), and calculated solid solution C amount.

  In addition, regarding the confirmation of the metal structure and carbide precipitation, each stainless steel material is polished and then immersed in a mixed solution of hydrofluoric acid, nitric acid, and glycerin in a volume ratio of 1: 1: 2 for etching. This was confirmed by observation with an optical microscope.

  Table 2 shows the manufacturing process, solid solution C amount, metallographic structure, and carbide precipitation state of each stainless steel material in Table 1.

  Steel type number A1 is the present example. In the stainless steel material having the composition of steel type number A in Table 1, annealing was performed at a material temperature of 760 ° C. and a soaking time of 12 hours as a first heat treatment, and a stainless steel material having a thickness of 3 mm was obtained. After cold rolling to a plate thickness of 1 mm, annealing is performed as a second heat treatment at a material temperature of 790 ° C. and a soaking time of 60 s. The solid solution C amount is 0.017% by mass, and the metal structure is composed of a single phase structure in which the parent phase is a ferrite phase, and carbides are uniformly precipitated.

  Steel type number B1 is this example. In the stainless steel material having the composition of steel type number B in Table 1, annealing was performed at a material temperature of 770 ° C. and a soaking time of 6 hours as a first heat treatment, and a stainless steel material having a thickness of 3 mm was obtained. After cold rolling to a plate thickness of 1 mm, annealing was performed as a second heat treatment at a material temperature of 820 ° C. and a soaking time of 60 s. The solid solution C amount is 0.024 mass%, and the metal structure is composed of a single phase structure in which the parent phase is a ferrite phase, and carbides are uniformly precipitated.

  Steel type number B2 is this example. In the stainless steel material having the composition of steel type number B in Table 1, annealing was performed at a material temperature of 830 ° C. and a soaking time of 6 hours as a first heat treatment to obtain a stainless steel material having a thickness of 3 mm. After cold rolling to a plate thickness of 1 mm, annealing was performed at a material temperature of 780 ° C. and a soaking time of 60 s as a second heat treatment. The solid solution C content is 0.018% by mass, and the metal structure is composed of a multiphase structure in which the parent phase is a ferrite phase and a martensite phase, and carbides are uniformly precipitated.

  Steel type number C1 is the present example, and in the stainless steel material having the composition of steel type number C in Table 1, annealing was performed at a material temperature of 710 ° C. and a soaking time of 8 hours as the first heat treatment to obtain a stainless steel material having a thickness of 3 mm. After cold rolling to a plate thickness of 1 mm, annealing was performed at a material temperature of 700 ° C. and a soaking time of 60 s as a second heat treatment. The solid solution C content is 0.015% by mass, and the metal structure is composed of a single-phase structure in which the parent phase is a martensite phase, and carbides are uniformly precipitated.

  Steel type number C2 is a comparative example. In the stainless steel material having the composition of steel type number C shown in Table 1, annealing was performed at a material temperature of 720 ° C. and a soaking time of 8 hours as the first heat treatment, and a stainless steel material having a thickness of 3 mm was obtained. After cold rolling to a thickness of 1 mm, annealing was performed as a second heat treatment at a material temperature of 1000 ° C. and a soaking time of 60 s. Further, heat treatment was performed at a material temperature of 700 ° C. and a soaking time of 1 h to precipitate carbides at the crystal grain boundaries. Further, the amount of dissolved C is 0.012% by mass, the metal structure is composed of a single-phase structure in which the parent phase is a martensite phase, and carbide is preferentially precipitated at the crystal grain boundaries.

  Steel type number C3 is a comparative example. In the stainless steel material having the composition of steel type number C in Table 1, annealing was performed at a material temperature of 720 ° C. and a soaking time of 8 hours as the first heat treatment, and a stainless steel material having a plate thickness of 3 mm was obtained. After cold rolling to a thickness of 1 mm, annealing was performed as a second heat treatment at a material temperature of 1000 ° C. and a soaking time of 60 s. The solid solution C amount is 0.081% by mass, and the metal structure is composed of a single phase structure of martensite phase, and the carbide is solid-solved in the mother phase almost entirely, and the carbide is almost precipitated. Not.

  Steel type number D1 is a comparative example. In the stainless steel material having the composition of steel type number D in Table 1, annealing was performed at a material temperature of 710 ° C. and a soaking time of 8 hours as the first heat treatment, and a stainless steel material having a thickness of 3 mm was obtained. After cold rolling to a thickness of 1 mm, annealing was performed as a second heat treatment at a material temperature of 700 ° C. and a soaking time of 60 s. Further, since the content of C is small, the amount of solid solution C is also as small as 0.009% by mass, and the metal structure is composed of a single-phase structure in which the parent phase is a martensite phase, and carbides are hardly precipitated.

  Steel type number E1 is a comparative example. In the stainless steel material having the component composition of steel type number E in Table 1, annealing was performed at a material temperature of 920 ° C. and a soaking time of 60 h as the first heat treatment, and a stainless steel material having a thickness of 3 mm was obtained. After cold rolling to a thickness of 1 mm, annealing was performed as a second heat treatment at a material temperature of 900 ° C. and a soaking time of 60 s. Further, since the content of C is small, the amount of solute C is as small as 0.006% by mass, and the metal structure is composed of a single phase structure in which the parent phase is a ferrite phase, and carbides are hardly precipitated.

  Steel type number F1 is a comparative example. In the stainless steel material having the component composition of steel type number F in Table 1, annealing is performed at a material temperature of 1080 ° C. and a soaking time of 60 hours as the first heat treatment, as in the normal manufacturing process of SUS304. After the cold rolling of a stainless steel material with a plate thickness of 3 mm to a plate thickness of 1 mm, annealing was further performed as a second heat treatment at a material temperature of 1090 ° C. and a soaking time of 60 s. Moreover, the amount of solute C is 0.068 mass%, and the metal structure is composed of a single phase structure in which the parent phase is an austenite phase, and carbides are hardly precipitated.

  Although omitted in Table 2, in each stainless steel material, the scale was removed by pickling after annealing.

  In the stainless steel materials shown in Table 2, the joints were joined by high-frequency welding to produce pipes, and stainless steel pipes having an outer diameter of 38.1 mm were prepared. In these stainless steel pipes, workability evaluation and corrosion resistance evaluation were performed.

  For workability evaluation, each stainless steel pipe was visually checked for the presence of cracks and surface flaws after pipe making. The case where it was not confirmed was evaluated as ◯, and the case where it was confirmed was rated as ×.

The corrosion resistance was evaluated by performing a cast test in accordance with the JIS H8502 cast test method after removing the scale of the joint with a grinder. The test solution for the cast test was 5 mass% NaCl (sodium chloride aqueous solution) +0.268 g / LCuCl ₂ (copper chloride) + CH ₃ COOH (acetic acid) adjusted to pH 3.0 to 3.1, and the test temperature was The temperature was 50 ± 2 ° C. In the cast test, the side constant of each stainless steel plate is set to 2, these stainless steel plates are set in a test tank, and the test solution is sprayed. Then, after 200 hours, the presence or absence of rusting in the mother phase and the joint was visually confirmed, and the case where it was not confirmed was rated as ◯, and the case where it was confirmed was marked as x.

  Table 3 shows the results of workability evaluation and corrosion resistance evaluation.

  As shown in Table 3, in the high-strength stainless steel pipes of steel type numbers A1, B1, B2, and C1, which are the present examples, none of the cracks and surface flaws were confirmed after pipe formation, and the flaws after the cast test Since it was not confirmed, workability and corrosion resistance are good.

  On the other hand, in the stainless steel pipe of steel type No. C2 in which carbide is preferentially precipitated at the grain boundaries, cracking has been confirmed, and the workability is insufficient. This is presumably because the carbide is preferentially precipitated at the grain boundaries, so that the toughness is lowered and the workability is deteriorated. In addition, rust is confirmed in the parent phase and the joint, and the corrosion resistance is insufficient. This is presumably because the carbide was precipitated locally at the crystal grain boundaries, so that a Cr-deficient layer was formed around the carbide and the corrosion resistance was lowered.

  In the comparative example, the stainless steel pipe of steel type No. C3 in which C was dissolved in almost all of the matrix, because of the high strength at the time of pipe making, pipe making was difficult, and surface flaws were confirmed. Insufficient sex. This is considered because the amount of solid solution C exceeded 0.03% by mass, and thus the strength was excessively increased and the workability was deteriorated. In addition, since corrosion is confirmed at the joint, the corrosion resistance is insufficient. This is because the amount of solute C exceeded 0.03% by mass, so a large amount of carbides precipitated in the joint during the cooling process during pipe forming, and a Cr-depleted layer was formed in the joint due to the formation of this carbide. Thus, it is considered that the corrosion resistance of the joint portion has decreased.

  As for the stainless steel pipes of steel type numbers D1 and E1, which are comparative examples, neither cracking nor surface flaws were confirmed after pipe formation, and no flaws after casting test were confirmed, so that workability and corrosion resistance were good.

  The stainless steel pipe of steel type F1, which is a comparative example and is normal SUS304, has good workability because no cracks and surface defects were confirmed after pipe making. However, since corrosion was confirmed at the joint after the cast test, the corrosion resistance is insufficient. This is because the amount of solute C exceeded 0.03% by mass, a large amount of carbides precipitated in the joint during the cooling process during pipe forming, and a Cr-depleted layer was formed by this carbide formation, It is thought that the corrosion resistance of the steel decreased.

  The results of workability evaluation and corrosion resistance evaluation shown in Table 3 were good, and heat treatment after pipe forming was performed on stainless steel pipes of steel type numbers A1, B1, B2, C1, D1, E1, metal structure investigation, carbide precipitation Existence investigation, tensile strength measurement, and corrosion resistance evaluation were performed.

  Steel type number A1-1 is a present Example, and after heat-treating the stainless steel pipe of steel type number A1 in Table 3 at a material temperature of 980 ° C. and a soaking time of 60 s.

  Steel type number A1-2 is a comparative example, and the heat treatment after pipe forming is not performed on the stainless steel pipe of steel type number A1 in Table 3, and the carbides are still deposited.

  Steel type number B1 is the present example, and after heat-treating the stainless steel pipe of steel type number B1 in Table 3 at a material temperature of 1030 ° C. and a soaking time of 60 s.

  Steel type number B2 is this example, and after heat-treating a stainless steel pipe of steel type number B2 in Table 3 at a material temperature of 1030 ° C. and a soaking time of 60 s.

  Steel type number C1 is this example, and after heat-treating a stainless steel pipe of steel type number C1 in Table 3 at a material temperature of 1050 ° C. and a soaking time of 60 s, the heat treatment is performed.

  Steel type number D1 is a comparative example, in which a stainless steel pipe having a steel type number D1 in Table 3 was formed and then heat-treated at a material temperature of 1030 ° C. and a soaking time of 60 s.

  Steel type number E1 is a comparative example, in which a stainless steel pipe of steel type number E1 in Table 3 was formed and then heat-treated at a material temperature of 1000 ° C. and a soaking time of 60 s.

  The investigation of the presence of metal structure and carbide was performed by the same method as the measurement method for the stainless steel plate described above in the parent phase and the joint.

  Tensile strength was measured by chucking both ends of a 300 mm long stainless steel pipe and performing a tensile test at a crosshead speed of 3 mm / min.

  Corrosion resistance evaluation was evaluated by a combined salt / wet cycle test, which is a more severe condition than the above-mentioned cast test in consideration of a more severe use environment. The salt dry-wet combined test is a salt spray process in which 5 mass% NaCl (sodium chloride) is sprayed at 35 ° C. for 900 s on a test piece having a length of 150 mm, and is maintained at 3.6 ks in an environment with an atmospheric temperature of 60 ° C. and a humidity of 35% This is a test method in which the drying step and the wetting step of holding 10.8 ks in an environment with an atmospheric temperature of 50 ° C. and a humidity of 95% are repeated for 5 cycles, and the presence or absence of rust is confirmed visually.

  Table 4 shows the results of the metal structure presence / absence investigation, carbide precipitation / existence investigation, tensile strength measurement, and corrosion resistance evaluation results.

As shown in Table 4, the high-strength stainless steel pipes of steel types A1-1, B1, B2, and C1, which are the present examples, have a tensile strength of 1200 (N / mm ² ) or more and a high strength. is there. Moreover, no corrosion is confirmed in the corrosion resistance evaluation, and the corrosion resistance is good.

The stainless steel pipe of steel type number A1-2, which is a comparative example, has a tensile strength of 610 (N / mm ² ) and is insufficient in strength. In addition, rusting was observed in the corrosion resistance evaluation, and the corrosion resistance was insufficient. This is because the heat treatment after pipe forming was not performed, so that carbide was precipitated, and further, the matrix and the joint were composed of a single-phase structure of a ferrite phase, so that the strength and corrosion resistance were insufficient. Conceivable.

The stainless steel pipe of steel type number D1, which is a comparative example, has good corrosion resistance, but has a tensile strength of 865 (N / mm ² ) and is insufficient in strength. This is considered that the strength of the component composition of the stainless steel material as the base material is insufficient because the C content is less than the C content defined in the present invention.

The stainless steel pipe of steel type number E1, which is a comparative example, has good corrosion resistance, but has a tensile strength of 545 (N / mm ² ) and is insufficient in strength. This is because SUS430LX, which is a conventional example, is used as a stainless steel material as a base material, the C content is less than the C content defined in the present invention, and the parent phase and the joint portion have a single phase structure of a ferrite phase. It is considered that the strength is insufficient because the parent phase is formed.

  As described above, the workability, strength, and corrosion resistance of the high-strength stainless steel pipe can be improved when the stainless steel material having the specified component composition is in the state before and after the specified pipe making.

  For stainless steel pipes of steel type numbers A1-1, A1-2, B1, B2, and C1 shown in Table 4 and steel type number C3 shown in Table 3, heat treatment was performed after pipe forming, roundness evaluation, cracking by flattening test Resistance evaluation and dimensional accuracy evaluation after bending were performed. In addition, about steel type number A1-2, C3, it has not heat-processed after pipe making.

  In the roundness evaluation, the diameter is measured at 8 points of 45 ° intervals around the axis of the pipe, and if the difference between the maximum value and the minimum value of these 8 points is within 0.2 mm, the roundness is It was good and was evaluated as ◯, and when it exceeded 0.2 mm, the roundness was insufficient and was evaluated as x.

  In the crack resistance evaluation by the flat test, the stainless steel pipe was set so that the weld bead portion of the stainless steel pipe having a length of 300 mm was perpendicular to the compression direction, and compressed to 19.05 mm, which was half the pipe diameter. And after compression, the presence or absence of the crack was confirmed visually. In addition, when a crack is not confirmed, it is (circle), and when a crack is confirmed, it is set as x.

  For evaluation of dimensional accuracy after bending, the raw pipe was set so that the weld bead portion was outside the bend, and the bending bending process was performed 30 times with a set bending angle of 130 °. After bending, the actual angle is measured with a protractor. If the actual angle variation is within 1 °, the dimensional accuracy is good. If it exceeds 1 °, the dimensional accuracy is insufficient. And x.

  Table 5 shows the results of the roundness evaluation, crack evaluation, and dimensional accuracy evaluation.

  As shown in Table 5, all of the steel type numbers A1-1, B1, B2, and C1 stainless steel pipes of this example were good in roundness, crack resistance, and dimensional accuracy.

  On the other hand, in the stainless steel pipe of steel type number A1-2 that is a comparative example, the dimensional accuracy was insufficient. This is because carbide is precipitated in the parent phase and the joint before pipe making, and the carbide is dissolved only in the joint by melt welding during pipe making, and heat treatment is not performed after pipe making. In other words, the carbide is not dissolved in the matrix, and the carbide is in a solid solution at the joint, and the hardness of the matrix and the joint is non-uniform. Conceivable.

  Further, the roundness of the stainless steel pipe of steel type number C3, which is a comparative example, was insufficient. This is probably because the roundness after pipe forming was insufficient because C was dissolved in the parent phase and the joint by the second heat treatment, and it was difficult to make pipes with high strength. Furthermore, the dimensional accuracy was insufficient. This is because C was dissolved in the parent phase and the joint before pipe forming, and carbides were precipitated only at the joint in the cooling step during pipe forming. And since heat treatment was not performed after the pipe making, C was dissolved in the mother phase, and C was not dissolved in the joint, and the hardness of the mother phase and the joint became non-uniform. Therefore, the dimensional accuracy is thought to have deteriorated.

  As described above, when the stainless steel material having the specified component composition is in the state before the specified pipe making and the state after the pipe forming, the workability and dimensional accuracy of the high-strength stainless steel pipe can be improved.

Claims (3)

By mass%, C: 0.04 to 0.12%, Ni: 0 (including no addition) to 5.0%, Cr: 12.0 to 17.0%, N: 0 (including no addition) -0.10%, Si: 0.2-2.0%, Mn: 2.0% or less, Cu: 0 (including no addition) to 2.0%, P: 0.06% or less, S: It contains 0.006% or less, the balance is Fe and inevitable impurities, and the parent phase is either a single phase structure of ferrite phase, a single phase structure of martensite phase, or a multiphase structure of ferrite phase and martensite phase The constructed stainless steel material is used as a base material.
Piped by melting and welding the end of this base material as a joint,
The parent phase is such that carbides are uniformly precipitated in the crystal grain boundaries and in the crystal grains and the solid solution C amount is adjusted to 0.03% or less,
The high-strength stainless steel pipe, wherein the joint has a molten structure formed by fusion welding. 2. The high-strength stainless steel pipe according to claim 1, wherein the matrix and the joint are formed by dissolving precipitated carbides by heat treatment after pipe forming. The high-strength stainless steel pipe according to claim 2, wherein the parent phase and the joint after heat treatment are composed of a single-phase structure of martensite phase or a multi-phase structure of martensite phase and ferrite phase.