Steel pipe or tube for pressure vessels, method of producing steel pipe or tube for pressure vessels, and composite pressure vessel liner

Abstract

A steel pipe or tube for pressure vessels having excellent quench crack resistance is provided. The steel pipe or tube for pressure vessels comprises: a specific chemical composition; and a metallic microstructure in which an average grain size of prior austenite grains is 500 μm or less, and an area fraction of microstructures other than ferrite is 50% or more.

Claims

1. A steel pipe or tube for pressure vessels, comprising: a chemical composition consisting of, in mass %, C: 0.30% to 0.60%, Si: 0.01% to 2.0%, Mn: 0.5% to 5.0%, P: 0.0001% to 0.020%, S: 0.0001% to 0.010%, N: 0.0001% to 0.010%, Al: 0.01% to 0.06%, and optionally one or more selected from Mo: 0.005% to 2.0%, and Cr: 0.005% to 3.0%, and one or more selected from Ni: 0.005% to 5.0%, and V: 0.05% to 0.35%, with the balance being Fe and inevitable impurities; and a metallic microstructure in which an average grain size of prior austenite grains is 50 μm or more and 500 μm or less, and an area fraction of microstructures other than ferrite is 50% or more, and a wall thickness of the steel pipe or tube for pressure vessels is 30 mm or more.

2. The steel pipe or tube for pressure vessels according to claim 1, wherein the chemical composition satisfies a relationship of the following Expression (1):
[Mn]+1.30×[Cr]+2.67×[Mo]+0.30×[Ni]≥2.15  (1) where brackets in the Expression (1) indicate a content, in mass %, of an element in the brackets, and indicate 0 in the case where the element is not contained.

3. The steel pipe or tube for pressure vessels according to claim 2, wherein the chemical composition satisfies a relationship of the following Expression (2):
[Mn]+1.30×[Cr]+2.67×[Mo]+0.30×[Ni]≥2.90  (2) where brackets in the Expression (2) indicate a content, in mass %, of an element in the brackets, and indicate 0 in the case where the element is not contained.

4. A method of producing the steel pipe or tube for pressure vessels of claim 1, comprising: heating a billet having the chemical composition according to claim 1, to a temperature of 1350° C. or less; rolling and pipe-or-tube-expanding the heated billet under a condition that a pipe or tube expansion finish temperature is 820° C. or more, to obtain a steel pipe or tube whose final wall thickness is 8.5% or more and less than 25.0% of a diameter of the billet; and cooling the steel pipe or tube obtained in the rolling and pipe-or-tube-expanding, under a condition that an average cooling rate from 800° C. to 300° C. is 1° C./s or more.

5. A method of producing the steel pipe or tube for pressure vessels of claim 2, comprising: heating a billet having the chemical composition according to claim 2, to a temperature of 1350° C. or less; rolling and pipe-or-tube-expanding the heated billet under a condition that a pipe or tube expansion finish temperature is 820° C. or more, to obtain a steel pipe or tube whose final wall thickness is 8.5% or more and less than 25.0% of a diameter of the billet; and cooling the steel pipe or tube obtained in the rolling and pipe-or-tube-expanding, under a condition that an average cooling rate from 800° C. to 300° C. is 0.5° C./s or more.

6. A method of producing the steel pipe or tube for pressure vessels of claim 3, comprising: heating a billet having the chemical composition according to claim 3, to a temperature of 1350° C. or less; rolling and pipe-or-tube-expanding the heated billet under a condition that a pipe or tube expansion finish temperature is 820° C. or more, to obtain a steel pipe or tube whose final wall thickness is 8.5% or more and less than 25.0% of a diameter of the billet; and cooling the steel pipe or tube obtained in the rolling and pipe-or-tube-expanding, under a condition that an average cooling rate from 800° C. to 300° C. is 0.2° C./s or more.

7. A composite pressure vessel liner, comprising the steel pipe or tube for pressure vessels according to claim 1.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) In the accompanying drawings:

(2) FIG. 1 is a diagram illustrating the shape of a test piece used in quench crack resistance evaluation.

DETAILED DESCRIPTION

(3) Detailed description is given below. In the following description, the term “pressure vessel” encompasses both a “composite pressure vessel” (Type 2 pressure vessel) produced by coating the periphery of a liner with carbon fiber reinforced plastic or the like and a “pressure vessel” (Type 1 pressure vessel) without a coating of carbon fiber reinforced plastic or the like. The term “steel pipe or tube for pressure vessels” encompasses both a steel pipe or tube used to produce a Type 1 pressure vessel and a steel pipe or tube used as a liner of a Type 2 pressure vessel.

(4) [Metallic Microstructure]

(5) A steel pipe or tube for pressure vessels according to one of the disclosed embodiments has a metallic microstructure in which the average grain size of prior austenite grains is 500 μm or less and the area fraction of microstructures other than ferrite is 50% or more. The reasons for limiting the metallic microstructure of the steel pipe or tube for pressure vessels in this way are explained below. Herein, “%” regarding metallic microstructure denotes an area fraction unless otherwise noted.

(6) Average grain size of prior austenite grains: 500 μm or less

(7) A larger average grain size of prior austenite grains (hereafter also referred to as “prior y grain size”) contributes to improved quench hardenability, and thus facilitates the obtainment of martensite microstructure. In a thick steel pipe or tube with a wall thickness of 20 mm or more, if the prior y grain size is excessively large, the prior y grain size in heat treatment is excessively large, which makes it difficult to suppress quench cracks. The prior y grain size is therefore 500 μm or less. The prior y grain size is preferably 400 μm or less. No lower limit is placed on the prior y grain size, yet an excessively small prior y grain size causes an increase in production cost. Accordingly, the prior y grain size is preferably more than 20 μm, and more preferably 50 μm or more. If the priory grain size is more than 20 μm, ferrite microstructure after heat treatment can be reduced. Consequently, the strength can be ensured easily, and the reduction of area can be improved. This further improves the reliability of the pressure vessel.

(8) Area fraction of microstructures other than ferrite: 50% or more

(9) If the total area fraction of microstructures other than ferrite to the whole metallic microstructure (hereafter also referred to as “area fraction other than ferrite”) is less than 50%, the prior y grain size in heat treatment is excessively large, which makes it difficult to suppress quench cracks. The area fraction other than ferrite is therefore 50% or more. The area fraction other than ferrite is preferably 60% or more, further preferably 70% or more, and most preferably 90% or more. A higher area fraction other than ferrite is more desirable, and thus the area fraction other than ferrite may be 100% at the maximum.

(10) The microstructures other than ferrite preferably include at least one of martensite and bainite. The total area fraction of martensite and bainite to the whole metallic microstructure is preferably 50% or more, more preferably 70% or more, and further preferably 90% or more. A higher total area fraction of martensite and bainite is more desirable, and thus the total area fraction of martensite and bainite may be 100% at the maximum.

(11) [Chemical Composition]

(12) In the present disclosure, it is also important that the steel pipe or tube for pressure vessels has the chemical composition described above. The reasons for limiting the chemical composition in the present disclosure are explained below. Herein, “%” regarding components denotes mass % unless otherwise noted.

(13) C: 0.10% to 0.60%

(14) C is an element necessary to increase the strength of the pressure vessel. A liner after quenching and tempering preferably has a tensile strength of 800 MPa or more. To obtain such strength, the C content is 0.10 or more. The C content is preferably 0.33% or more. If the C content is more than 0.60%, quench cracks occur. The C content is therefore 0.60% or less. The C content is preferably 0.45% or less.

(15) Si: 0.01% to 2.0%

(16) Si is an element that contributes to improved strength by solid solution strengthening. To achieve the effect, the Si content is 0.01% or more. The Si content is preferably 0.15% or more. If the Si content is more than 2.0%, the effect is saturated. Besides, the surface characteristics of the steel material degrade, and rollability decreases. The Si content is therefore 2.0% or less. The Si content is preferably 0.5% or less.

(17) Mn: 0.5% to 5.0%

(18) Mn is an element that contributes to improved strength by solid solution strengthening and quench hardenability improvement. Mn also suppresses excessive coarsening of prior austenite grains and ferrite transformation. To achieve these effects, the Mn content is 0.5% or more. The Mn content is preferably 0.6% or more. If the Mn content is more than 5.0%, the effects are saturated, and also rolling and forming are difficult. Besides, if the Mn content is more than 5.0%, austenite remains after heat treatment following liner forming, causing a decrease in fatigue resistance. The Mn content is therefore 5.0% or less. The Mn content is preferably 1.5 or less.

(19) P: 0.0001% to 0.020%

(20) P is an element that contributes to improved strength by solid solution strengthening, but our study revealed that P decreases the quench crack resistance of the steel. If the P content is more than 0.020%, quench cracks occur in liner heat treatment. To improve the quench crack resistance, it is very important that the P content is 0.020% or less. The P content is preferably 0.015% or less, and more preferably 0.010% or less. Excessively reducing P so that the P content is less than 0.0001% increases the production cost in the steelmaking process. The P content is therefore 0.0001% or more.

(21) S: 0.0001% to 0.010%

(22) Excessive S causes hot red shortness, which may lead to manufacturing defects. S also forms MnS as an inclusion, and decreases toughness. These problems do not occur as long as the S content is 0.010% or less. The S content is therefore 0.010% or less. The S content is preferably 0.0050% or less, and more preferably 0.0030% or less. Excessively reducing S so that the S content is less than 0.0001% increases the desulfurization cost in the steelmaking process. The S content is therefore 0.0001% or more.

(23) The total content of P and S is preferably 0.025% or less, in terms of improving toughness.

(24) N: 0.0001% to 0.010%

(25) N has little influence on the fatigue resistance of the steel material, and the advantageous effects according to the present disclosure are not lessened if the N content is 0.010% or less. The N content is therefore 0.010% or less. The N content is preferably 0.006% or less, and more preferably 0.004% or less. The N content is desirably low in terms of improving toughness. However, excessively reducing N increases the cost in steelmaking, and so the N content is 0.0001% or more. The N content is preferably 0.0010% or more.

(26) Al: 0.01% to 0.06%

(27) Al is an element effective as a deoxidizer in the steelmaking process. To achieve the effect, the Al content is 0.01% or more. The Al content is preferably 0.02% or more. If the Al content is more than 0.06%, the effect is saturated. The Al content is therefore 0.06% or less.

(28) The steel pipe or tube for pressure vessels according to one of the disclosed embodiments has a chemical composition containing the components described above with the balance being Fe and inevitable impurities.

(29) In another one of the disclosed embodiments, the chemical composition may further contain one or more selected from the group consisting of Mo: 0.005% to 2.0% and Cr: 0.005% to 3.0%.

(30) Mo: 0.005% to 2.0%

(31) Mo is an element that improves quench hardenability, and has a function of contributing to higher liner strength and improving the quench hardenability of the steel material to increase the ratio of microstructures (in particular, martensite and lower bainite) other than ferrite in the metallic microstructure. Mo also suppresses ferrite transformation to improve the quench crack resistance. Furthermore, by adding Mo, the cooling rate necessary to obtain the above-described metallic microstructure can be lowered, and the risk of quench cracks in liner heat treatment can be reduced. To achieve these effects, in the case of adding Mo, the Mo content is 0.005% or more. The Mo content is preferably 0.10% or more. If the Mo content is more than 2.0%, the effects are saturated, and higher cost is required. The Mo content is therefore 2.0% or less. The Mo content is preferably 1.0% or less, more preferably 0.5% or less, and further preferably 0.3% or less.

(32) Cr: 0.005% to 3.0%

(33) Cr is an element that improves quench hardenability, and has a function of contributing to higher liner strength and improving the quench hardenability of the steel material to increase the ratio of microstructures (in particular, martensite and lower bainite) other than ferrite in the metallic microstructure. Cr also suppresses ferrite transformation to improve the quench crack resistance. Furthermore, by adding Cr, the cooling rate necessary to obtain the above-described microstructure can be lowered, and the risk of quench cracks in liner heat treatment can be reduced. Cr also suppresses coarsening of prior austenite grains. To achieve these effects, in the case of adding Cr, the Cr content is 0.005% or more. The Cr content is preferably 0.1% or more, more preferably 0.5% or more, and further preferably 0.7% or more. If the Cr content is more than 3.0%, the effects are saturated, and higher cost is required. The Cr content is therefore 3.0% or less. The Cr content is preferably 2.0% or less, and more preferably 1.5% or less.

(34) In another one of the disclosed embodiments, the chemical composition may further contain one or more selected from the group consisting of Ni: 0.005% to 5.0% and V: 0.05% to 0.35%, in addition to the elements described above.

(35) Ni: 0.005% to 5.0%

(36) Ni is an element that improves quench hardenability, and has a function of contributing to higher liner strength and improving the quench hardenability of the steel material to increase the ratio of microstructures (in particular, martensite and lower bainite) other than ferrite in the metallic microstructure. Ni also suppresses ferrite transformation to improve the quench crack resistance. Furthermore, by adding Ni, the cooling rate necessary to obtain the above-described microstructure can be lowered, and the risk of quench cracks in liner heat treatment can be reduced. Ni also suppresses coarsening of prior austenite grains. To achieve these effects, in the case of adding Ni, the Ni content is 0.005% or more. The Ni content is preferably 0.5% or more. If the Ni content is more than 5.0%, the effects are saturated, and higher cost is required. The Ni content is therefore 5.0% or less. For cost reduction, the Ni content is preferably 3.0% or less, and more preferably 2.0% or less.

(37) V: 0.05% to 0.35%

(38) V is an element effective in improving hardness and strength (yield point, tensile strength) when used in combination with other elements such as Cr and Mo. To achieve the effect, in the case of adding V, the V content is 0.05% or more. If the V content is more than 0.35%, carbide coarsens, and the steel may become brittle. Accordingly, the V content is 0.35% or less.

(39) The chemical composition preferably satisfies the relationship of the following Expression (1):
[Mn]+1.30×[Cr]+2.67×[Mo]+0.30×[Ni]≥2.15  (1)

(40) (where the brackets in Expression (1) indicate the content (mass %) of the element in the brackets, and indicate 0 in the case where the element is not contained).

(41) When the chemical composition of the steel pipe or tube for pressure vessels satisfies the relationship of Expression (1), the quench hardenability of the steel is improved, so that microstructures other than ferrite can be obtained more easily, and the necessary cooling rate can be lowered. Moreover, the risk of quench cracks in liner heat treatment can be reduced.

(42) The chemical composition preferably satisfies the relationship of the following Expression (2):
[Mn]+1.30×[Cr]+2.67×[Mo]+0.30×[Ni]≥2.90  (2)

(43) (where the brackets in Expression (2) indicate the content (mass %) of the element in the brackets, and indicate 0 in the case where the element is not contained).

(44) When the chemical composition of the steel pipe or tube for pressure vessels satisfies the relationship of Expression (2), the quench hardenability of the steel is further improved, so that microstructures other than ferrite can be obtained very easily, and the necessary cooling rate can be further lowered. Moreover, the risk of quench cracks in liner heat treatment can be further reduced.

(45) No upper limit is placed on the value of the left side in Expressions (1) and (2), yet the upper limit may be 15.74 determined from the upper limits of the contents of Mn, Cr, Mo, and Ni. In other words, the chemical composition may satisfy the relationship of the following Expression (3):
15.74[Mn]+1.30×[Cr]+2.67×[Mo]+0.30×[Ni]  (3).

(46) [Shape]

(47) The steel pipe or tube for pressure vessels according to the present disclosure is preferably a seamless steel pipe or tube.

(48) [Wall Thickness]

(49) Wall thickness: 30 mm or more

(50) If the wall thickness of the steel pipe or tube for pressure vessels is 30 mm or more, the obtained liner's share of stress can be further increased. This reduces the usage of CFRP, and contributes to lower cost of composite pressure vessels. The fatigue limit in high-pressure hydrogen can be further improved by forming a steel pipe or tube with a wall thickness of 30 mm or more to obtain a liner and then subjecting the liner to autofrettage to apply residual compressive stress to the inside of the liner. The wall thickness of the steel pipe or tube for pressure vessels is therefore preferably 30 mm or more, more preferably 35 mm or more, and further preferably 40 mm or more. If the wall thickness is excessively thick, the stress of the outside of the liner may become excessively high during pressure storage. Besides, the necessary amount of alloy to obtain the desired microstructure increases, which requires higher cost. Accordingly, the wall thickness is preferably 80 mm or less, more preferably 70 mm or less, and further preferably 60 mm or less. A typical steel pipe or tube has uniform wall thickness in all parts. However, in the case where the wall thickness differs depending on position, it is preferable that the wall thickness of the steel pipe or tube in the longitudinal center is in the range described above. This is because, when the steel pipe or tube for pressure vessels is used as a pressure vessel or a pressure vessel liner, its longitudinal center is under maximum stress.

(51) [Production Method]

(52) A method of producing a steel pipe or tube for pressure vessels according to the present disclosure is described below.

(53) The steel pipe or tube for pressure vessels according to the present disclosure can be produced by performing the following (1) to (3) in order:

(54) (1) heating a billet;

(55) (2) rolling and pipe-or-tube-expanding the heated billet to obtain a steel pipe or tube; and

(56) (3) cooling the steel pipe or tube obtained in the rolling and pipe-or-tube-expanding.

(57) Each of these processes is described below. The temperatures in the following description of the heating, the rolling and pipe or tube expansion, and the cooling each denote the temperature of the outer surface of the billet or steel pipe or tube unless otherwise noted.

(58) [Heating]

(59) A billet having the chemical composition described above is heated in order to perform hot rolling. The billet is not limited, and may be, for example, a billet obtained by typical continuous casting.

(60) Heating temperature: 1350° C. or less

(61) If the heating temperature in the heating is more than 1350° C., the cost increases significantly. The heating temperature is therefore 1350° C. or less. The heating temperature is preferably 1300° C. or less. Although a lower heating temperature is more preferable, if the heating temperature is excessively low, the temperature of the raw material decreases before the final process, and the deformation resistance in the rolling and pipe or tube expansion increases. This makes the rolling and pipe or tube expansion difficult. The heating temperature is therefore preferably 950° C. or more, more preferably 1000° C. or more, and further preferably 1050° C. or more.

(62) [Rolling and Pipe or Tube Expansion]

(63) Next, the billet heated in the heating is rolled and pipe-or-tube-expanded to obtain a steel pipe or tube. The rolling may be hot rolling including piercing rolling by typical Mannesmann plug mill process or Mannesmann mandrel mill process.

(64) Pipe or tube expansion finish temperature: 820° C. or more

(65) If the pipe or tube expansion finish temperature is less than 820° C., the load of rolling and pipe or tube expansion increases, which makes the production difficult. The pipe or tube expansion finish temperature is therefore 820° C. or more. Moreover, if the pipe or tube expansion finish temperature is less than 820° C., it is hard to achieve an area fraction of microstructures other than ferrite of 50% or more. The pipe or tube expansion finish temperature is preferably 850° C. or more. Although no upper limit is placed on the pipe or tube expansion finish temperature, if the pipe or tube expansion finish temperature is excessively high, the metallic microstructure tends to be not uniform. The pipe or tube expansion finish temperature is therefore preferably 1200° C. or less, more preferably 1100° C. or less, and further preferably 1050° C. or less.

(66) Final wall thickness: 8.5% or more and less than 25.0% of billet diameter

(67) If the final wall thickness of the steel pipe or tube obtained as a result of the rolling and pipe or tube expansion (hereafter also simply referred to as “final wall thickness”) is 25.0% or more of the diameter of the billet used, strain is low, so that the prior y grain size exceeds 500 μm, causing insufficient quench crack resistance. Accordingly, the final wall thickness is less than 25.0% of the billet diameter. The final wall thickness is preferably 23.0% or less of the billet diameter, and more preferably 20.0% or less of the billet diameter. If the final wall thickness is excessively small as compared with the billet diameter, prior y grains are refined due to applied strain. This facilitates the formation of ferrite. Accordingly, the final wall thickness is 8.5% or more of the billet diameter. The final wall thickness is preferably 9.0% or more of the billet diameter.

(68) [Cooling]

(69) The steel pipe or tube obtained in the rolling and pipe or tube expansion is then cooled. Here, the cooling rate needs to be controlled in the below-described manner, in order to obtain the desired metallic microstructure. The cooling method is not limited, and any of the methods such as water cooling, oil quenching, and air cooling may be used singly or in combination.

(70) Average Cooling Rate from 800° C. to 300° C.: 1° C./s or More

(71) If the average cooling rate from 800° C. to 300° C. (hereafter also simply referred to as “average cooling rate”) is less than 1° C./s, ferrite forms at an area fraction of 50% or more. This causes an excessively large prior y grain size in liner heating, and makes it difficult to ensure quench crack resistance. The average cooling rate is therefore 1° C./s or more. Although no upper limit is placed on the average cooling rate, special equipment is needed in order to realize an excessively high cooling rate, which causes an increase in cost. The average cooling rate is therefore preferably 200° C./s or less.

(72) In the case where the chemical composition of the steel pipe or tube satisfies the relationship of Expression (1) as mentioned above, the desired microstructure can be obtained if the average cooling rate is 0.5° C./s or more. In the case where the chemical composition of the steel pipe or tube satisfies the relationship of Expression (2) as mentioned above, the desired microstructure can be obtained if the average cooling rate is 0.2° C./s or more.

(73) The cooling rate in a temperature range below 300° C. is not limited, and the steel pipe or tube can be cooled to room temperature under any conditions. This is because the transformation of the microstructure of the material basically ends at a temperature not lower than 300° C.

(74) [Pressure Vessel]

(75) A pressure vessel can be produced from the steel pipe or tube for pressure vessels obtained as described above. The method of producing the pressure vessel is not limited, and may be any method. Typically, the steel pipe or tube for pressure vessels is further subjected to heat treatment of quenching and tempering, to achieve mechanical properties required of pressure vessels. The heat treatment method differs depending on the required mechanical properties, yet typically the steel pipe or tube for pressure vessels is heated to 850° C. or more, then cooled, and then tempered in a temperature range of 400° C. or more and 700° C. or less, to adjust the mechanical properties.

(76) In the case where a decarburized layer resulting from the heat treatment is formed at the inner and/or outer surface of the steel pipe or tube after the heat treatment, the decarburized layer is removed because the metallic microstructure of the surface layer was changed. The roughness of the inner surface of the steel pipe or tube influences the fatigue resistance, and is therefore preferably as low as possible. It is more preferable to perform surface polishing. Specifically, cut finishing, polish finishing, or mirror finishing is preferable, and polish finishing or mirror finishing is more preferable. In the case where the steel pipe or tube is bent due to the heat treatment, the bend may be corrected by straightening.

(77) Further, both ends of the steel pipe or tube are sealed to obtain a pressure vessel. Examples of the sealing method include a method of shaping both ends of the steel pipe or tube in capsule form to cover the ends, and a method of providing a screw structure at both ends of the steel pipe or tube and attaching a lid to it. An O-ring or a back-up ring may be used to improve airtightness. The pressure vessel is further provided with an inlet and an outlet connectable with a gas exchange pipe.

(78) [Composite Pressure Vessel]

(79) The steel pipe or tube for pressure vessels according to the present disclosure can also be used as a composite pressure vessel liner. For example, a composite pressure vessel can be obtained by wrapping carbon fiber reinforced plastic (CFRP) around the surface of the pressure vessel produced as described above. Any carbon fibers such as PAN-based carbon fibers or pitch-based carbon fibers may be used.

Examples

(80) More detailed description is given below, based on examples. The following examples merely represent preferred examples, and the present disclosure is not limited to these examples.

(81) Pressure vessel steel pipes or tubes were produced using billets having the chemical compositions listed in Table 1. In the production, first, each billet was subjected to the processes of heating, rolling and pipe or tube expansion, and cooling in sequence. The conditions in each of the processes are listed in Table 2. The metallic microstructure, tensile strength, and quench crack resistance of each obtained steel pipe or tube for pressure vessels were then evaluated. The evaluation methods are as follows.

(82) (Average Grain Size of Prior Austenite Grains)

(83) From each obtained steel pipe or tube, a test piece was collected so that the position of ¼ of the wall thickness in the longitudinal center part of the steel pipe or tube was an observation position. A section of the test piece was etched using a saturated picric acid solution to reveal prior austenite crystal grain boundaries, and the metallic microstructure was photographed using an optical microscope. The obtained photograph was subjected to image analysis, to calculate the average grain size of prior austenite grains.

(84) (Metallic Microstructure)

(85) From each obtained steel pipe or tube, a test piece was collected so that the position of ¼ of the wall thickness in the longitudinal center part of the steel pipe or tube was an observation position. A section of the test piece was etched using a 3% nital solution. The section was then observed using a scanning electron microscope (SEM) at appropriate magnifications from 1000 to 5000, and the obtained image was analyzed to evaluate the type and area fraction of each microstructure. Retained austenite was measured by X-ray diffraction measurement.

(86) (Tensile Strength)

(87) Each steel pipe or tube was cut to a length of 150 mm, and subjected to heat treatment (quenching and tempering). In the heat treatment, the cut steel pipe or tube was held at 860° C. for 120 min, then water cooled, and tempered at 620° C. for 180 min. A round bar test piece of 7 mm in diameter was collected from the position of ¼ of the wall thickness of the steel pipe or tube after the heat treatment according to JIS Z 2201, and its tensile strength was measured.

(88) (Quench Crack Resistance)

(89) To evaluate the quench crack resistance of each steel pipe or tube, the quench crack frequency was calculated by the following method. First, ten test pieces were collected from the position of ¼ of the wall thickness of each obtained steel pipe or tube. The test pieces had the shape illustrated in FIG. 1. The test pieces were then quenched. The quenching was performed by heating each test piece at 860° C. for 120 min and then water cooling the test piece. Whether or not the test pieces after the quenching had cracks was examined, and the proportion of the number of cracked test pieces to the ten test pieces, i.e. (the number of quench-cracked test pieces/10)×100(%), was taken to be the quench crack frequency.

(90) As can be understood from the results listed in Table 2, the steel pipes or tubes satisfying the conditions according to the present disclosure had excellent tensile strength, and had excellent quench crack resistance with a quench crack frequency of 20% or less in the heat treatment. The fatigue crack propagation characteristics were also improved. On the other hand, the steel pipes or tubes of comparative examples not satisfying the conditions according to the present disclosure had insufficient quench crack resistance with a quench crack frequency of more than 20%.

(91) Thus, the liner steel pipe or tube according to the present disclosure has sufficient quench crack resistance. Such a steel pipe or tube for pressure vessels according to the present disclosure can be used to efficiently produce a pressure vessel or a composite pressure vessel liner, with it being possible to reduce the cost of pressure vessels.

(92) TABLE-US-00001 TABLE 1 Steel Chemical composition (mass %)*.sup.1 sample [Mn] + 1.3[Cr] + ID C Si Mn P S Al N Mo Cr Ni P + S 2.67[Mo] + 0.3[Ni] A 0.30 0.20 0.75 0.008 0.0030 0.03 0.0030 0.16 1.01 — 0.011 2.49 B 0.30 0.20 0.75 0.010 0.0030 0.03 0.0030 — — — 0.013 0.75 C 0.30 0.20 0.75 0.015 0.0030 0.03 0.0030 0.16 1.01 — 0.018 2.49 D 0.30 0.20 0.75 0.020 0.0030 0.03 0.0030 0.16 1.01 — 0.023 2.49 E 0.35 0.25 0.80 0.020 0.0031 0.04 0.0015 0.12 1.30 1.62 0.023 3.30 F 0.05 0.18 0.61 0.010 0.0029 0.03 0.0022 0.15 0.92 — 0.013 2.21 G 0.30 0.20 0.75 0.025 0.0030 0.03 0.0030 0.16 1.01 — 0.028 2.49 H 0.30 0.20 0.75 0.040 0.0030 0.03 0.0030 0.16 1.01 — 0.043 2.49 I 0.30 0.20 0.75  0.0003 0.0030 0.03 0.0030 0.16 1.01 — 0.003 2.49 J 0.45 0.20 0.75  0.0001 0.0001 0.01 0.0001 0.005 3.00 — 0.000 4.66 K 0.10 2.00 0.75  0.0001 0.0001 0.01 0.0100 2.00 1.01 — 0.000 7.40 L 0.60 0.01 0.75  0.0001 0.0100 0.06 0.0001 0.16 1.01 — 0.010 2.49 M 0.30 0.20 0.75  0.0001 0.0200 0.01 0.0001 0.16 1.01 — 0.020 2.49 N 0.35 0.25 1.00 0.020 0.0031 0.04 0.0015 0.12 1.30 3.00 0.023 3.91 O 0.35 0.25 5.00 0.020 0.0031 0.04 0.0015 0.12 0.005 0.005 0.023 5.33 Steel sample ID Condition of Expression (1) Condition of Expression (2) Ac.sub.3*.sup.2 (° C.) Remarks A Satisfied Not satisfied 788 Conforming steel B Not satisfied Not satisfied 795 Conforming steel C Satisfied Not satisfied 793 Conforming steel D Satisfied Not satisfied 796 Conforming steel E Satisfied Satisfied 760 Conforming steel F Satisfied Not satisfied 859 Comparative steel G Satisfied Not satisfied 800 Comparative steel H Satisfied Not satisfied 810 Comparative steel I Satisfied Not satisfied 782 Conforming steel J Satisfied Satisfied 728 Conforming steel K Satisfied Satisfied 966 Conforming steel L Satisfied Not satisfied 731 Conforming steel M Satisfied Not satisfied 780 Comparative steel N Satisfied Satisfied 733 Conforming steel O Satisfied Satisfied 673 Conforming steel *.sup.1the balance being Fe and inevitable impurities *.sup.2Ac.sub.3 (° C.) = 910-203[C].sup.1/2 − 30[Mn] + 44.7[Si] + 700[P] + 100[Al] + 31.5[Mo] − 11[Cr] − 15.2[Ni] − 20[Cu] + 104[V] where brackets in the expression indicate the content (mass %) of the element in the brackets, and indicate 0 in the case where the element is not contained.

(93) TABLE-US-00002 TABLE 2 Production conditions Rolling and pipe or tube expansion Pipe or tube Cooling Heating expansion Final wall Average Condition of Condition of Ac.sub.3 Heating finish Final wall thickness/ cooling Steel Expression Expression point temperature temperature thickness billet diameter rate*.sup.1 No. sample ID (1) (2) (° C.) (° C.) (° C.) (mm) (%) (° C./s) 1 A Satisfied Not satisfied 788 1200 860 60 17.1 15 2 A Satisfied Not satisfied 788 1200 750 60 17.1 15 3 A Satisfied Not satisfied 788 1200 860 60 40.0 15 4 B Not satisfied Not satisfied 795 1100 900 38 10.9 30 5 B Not satisfied Not satisfied 795 1100 900 38 10.9   0.7 6 C Satisfied Not satisfied 793 1250 950 46 13.1 10 7 D Satisfied Not satisfied 796 1150 850 46 22.0  5 8 E Satisfied Satisfied 760 1250 1000  46 13.1  1 9 E Satisfied Satisfied 760 1250 1000  100 30.3   0.5 10 E Satisfied Satisfied 760 1250 1000  35 10.6  1 11 E Satisfied Satisfied 760 1250 1000  30  6.0   0.2 12 F Satisfied Not satisfied 859 1200 900 50 14.3 30 13 G Satisfied Not satisfied 800 1200 860 60 17.1 15 14 H Satisfied Not satisfied 810 1200 860 60 17.1 15 15 I Satisfied Not satisfied 782 1150 850 46 22.0  5 16 J Satisfied Satisfied 728 1200 860 17.1 10   40 17 K Satisfied Satisfied 966 1200 860 17.1 10   40 18 L Satisfied Not satisfied 731 1200 860 17.1 10   40 19 M Satisfied Not satisfied 780 1200 860 17.1 10   40 20 N Satisfied Satisfied 733 1200 860 17.1 10   40 21 O Satisfied Satisfied 673 1200 860 17.1 10   40 Properties after heat Metallic microstructure treatment Area fraction Quench other than Prior γ Tensile crack ferrite Microstructures grain size strength frequency No. (%) other than ferrite*.sup.2 (μm) (MPa) (%) Remarks  1 100  M, B 150 913 0 Example  2 40 M, B, P  80 911 50 Comparative Example  3 100  M, B 600 910 50 Comparative Example  4 90 M, B 230 912 0 Example  5 20 B, P  60 875 40 Comparative Example  6 100  M, B 270 923 10 Example  7 95 M, B, RA  90 911 20 Example  8 98 M, B, RA 320 893 0 Example  9 80 M, B, RA 550 891 50 Comparative Example 10 98 M, B, RA 280 890 5 Example 11 40 B, P  10 756 25 Comparative Example 12 30 B, P 300 722 0 Comparative Example 13 100  M, B 150 906 40 Comparative Example 14 100  M, B 150 903 80 Comparative Example 15 95 M, B, RA  90 897 10 Example 16 95 M, B 155 950 0 Example 17 100  M 200 720 0 Example 18 100  M, B 160 1300  10 Example 19 95 M, B 150 900 25 Comparative Example 20 95 M, B 180 850 0 Example 21 95 M, B 190 900 0 Example *.sup.1average cooling rate from 800 to 300° C. *.sup.2M: martensite, B: bainite, F: ferrite, RA: retained austenite, P: pearlite