# Patent

## Title
Method for making high-strength high-toughness martensitic stainless steel seamless pipe

## Abstract

A method of producing a high-strength high-toughness martensitic stainless steel seamless pipe which includes heating a martensitic stainless steel raw material to an austenitic range and subjecting the raw material to piercing and elongating to form an original pipe. The original pipe is cooled to form a structure substantially composed of martensite in the original pipe. The original pipe is reheated to a temperature in the dual-phase range between the Ac1 transformation point and the Ac3 transformation point, and is subjected to finishing rolling at an initial rolling temperature T (° C.) between the Ac1 transformation point and the Ac3 transformation point. The original pipe is then cooled to form a processed pipe. The processed pipe is tempered at a temperature below the Ac1 transformation point. The reduction in area R in the finishing rolling step may be in the range of 10% to 90%, and the initial rolling temperature T and the reduction in area R may satisfy the relationship 800≦T−0.625R≦850.

## Background
BACKGROUND
1. Field of the Invention
This invention relates to a method for making a martensitic stainless steel seamless pipe. The seamless pipe has high corrosion resistance and is suitable for oil country tubular goods (OCTGs). In particular, the invention relates to improvements in toughness and a decrease in anisotropy of toughness.
2. Description of the Related Art
In consideration of the advance in crude oil prices and anticipated depletion of oil resources in the near future, deep stratum oil fields and highly corrosive sour gas fields are being developed all over the world.
These oil and gas fields generally spread out at very deep layers and in severely corrosive environments at high temperatures containing CO2, Cl− ions and the like. Thus, OCTGs used in these fields must have high toughness and high corrosion resistance. In general, under severe corrosive environments containing such CO2, Cl− ions and the like, martensitic stainless steel seamless pipes with high CO2 corrosion resistance containing 13% chromium are primarily used.
Martensitic stainless steel seamless pipes are generally produced by the following process: A raw steel material is heated to a temperature capable of piercing, and subjected to piercing using a piercing mill and elongating using a mandrel mill or plug mill to form an original pipe. The original pipe is reheated to an austenitic temperature range and subjected to finishing rolling using a hot stretch reducing mill or a sizing mill. After air-cooling, the composition of the seamless pipe comprises martensite. The seamless pipe is subjected to quenching from the austenitic temperature range and tempering at a temperature below the AC1 transformation point if higher strength and higher toughness are required.
Oil well pipes used in deteriorating well environments must have higher mechanical properties, such as higher toughness at low temperatures and higher resistance to sulfide stress cracking.
In order to satisfy such requirements, for example, Japanese Unexamined Patent Application Publication No. 1-123025 discloses a method for making a martensitic stainless steel seamless pipe. This method includes the steps of piercing and rolling a martensitic stainless steel slab at a temperature of 1,050° C. to 1,250° C.; cooling the rolled pipe at a cooling rate of 30° C./min to at least 500° C. and further cooling the pipe to a temperature below the martensite transformation temperature to form a steel structure containing at least 80% of martensite; reheating the pipe to a temperature between (Ac1 transformation point −200° C.) and Ac1 transformation point and finishing-rolling the pipe at a reduction in area of at least 5%; maintaining the pipe at the final finishing-rolling temperature or reheating the pipe to a temperature below the Ac1 transformation point immediately after the finishing rolling step, and then cooling the pipe by spontaneous or forced air cooling. Alternatively, after the step of forming the martensitic structure, this method may include the steps of reheating the pipe to a temperature between the (Ac1 transformation point −200° C.) and the Ac1 transformation point, finishing-rolling the pipe at a reduction in area of at least 5%, and then cooling the pipe by spontaneous or forced air cooling; reheating the pipe to a temperature below the Ac1 transformation point immediately after the finishing rolling step, and then cooling the pipe by spontaneous or forced air cooling.
However, the seamless pipe produced by this method has the following problem: Since the pipe is rolled at a non-recrystallization temperature range, the structure is elongated in the rolling direction. As a result, the toughness and corrosion resistance of the seamless pipe are high in the rolling direction, but low in the circumferential direction perpendicular to the rolling direction. In other words, the seamless pipe exhibits noticeable anisotropy in mechanical properties.
SUMMARY OF THE INVENTION
It would, therefore, be advantageous to provide a method for making a martensitic stainless steel seamless pipe having high strength, high toughness, and low anisotropy of mechanical properties, at low cost. In the invention, “high strength” means a yield strength YS of the pipe of about 551 MPa or more, and “high toughness” means an absorbed energy per unit area at −40° C. by the Charpy impact test (hereinafter referred to as “E−40”) is about 90 J/cm2 or more.
We intensively investigated the effects of finishing rolling conditions on toughness, and discovered that a seamless pipe having a fine martensitic structure with low anisotropy was obtained by reheating an original pipe that had been preliminarily treated so as to have a martensitic structure to a dual-phase temperature range at which both a ferritic (α) phase and an austenitic (γ) phase; finishing-rolling the pipe at a specific initial rolling temperature and a specific reduction in area; cooling the pipe; and tempering the pipe.
Hence, this invention is direct to a method for making a high-strength high-toughness martensitic stainless steel seamless pipe including an original pipe production step of heating a martensitic stainless steel raw material to an austenitic range, piercing and elongating the raw material to form an original pipe, cooling the original pipe to form a structure substantially composed of martensite in the original pipe; a finishing rolling step of reheating the original pipe to a temperature in the dual-phase range between the Ac1 transformation point and the Ac3 transformation point, finishing-rolling the original pipe at an initial rolling temperature T (° C.) between the Ac1 transformation point and the Ac3 transformation point, cooling the original pipe to form a processed pipe having a predetermined size; and tempering the processed pipe at a temperature below the Ac1 transformation point.
Preferably, the reduction in area R in the finishing rolling step is in the range of about 10% to about 90%, and the initial rolling temperature T and the reduction in area R satisfies the relationship: 800≦T−0.625R≦850.



BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 is a graph showing the effects of the reduction in area R and the initial rolling temperature T in finishing rolling on the toughness of a martensitic stainless steel seamless pipe; and
FIG. 2 is a schematic diagram showing a process for making the martensitic stainless steel seamless pipe in accordance with aspects of the invention.



DETAILED DESCRIPTION
Any known martensitic stainless steel can be used in the invention as a raw material for a martensitic stainless steel seamless pipe. A preferable composition of the martensitic stainless steel is as follows: about 0.005% by weight (hereinafter merely %) to about 0.30% C, about 0.10% to about 1.00% Si, about 0.05% to about 2.00% Mn, about 0.03% or less of P, about 0.005% or less of S, about 10.0% to about 15.0% Cr, about 0.001% to about 0.05% Al; and the balance Fe and incidental impurities. The composition may further contain at least one element of about 7.0% or less of Ni, about 3.0% or less of Mo, and about 3.0% or less of Cu; at least one element of about 0.2% or less of Nb, about 0.2% or less of V, about 0.3% or less of Ti, about 0.2% or less of Zr, about 0.0005% to about 0.01% B, and about 0.07% or less of N; and/or at least one element of about 0.0005% to about 0.01% Ca and about 0.0005% to about 0.01% REM (rare earth metals).
The reasons for the limitation of the composition will now be described.
C: About 0.005% to About 0.30%
Carbon (C) is an essential element for ensuring desired strength of the martensitic stainless steel seamless pipe. The desired strength is achieved at a C content of at least about 0.005%. However, a C content exceeding about 0.30% causes an increase in formation of course carbide grains that decrease toughness and corrosion resistance. Thus, the upper limit of the C content is preferably about 0.30% in the invention and more preferably about 0.22% to achieve higher corrosion resistance.
Si: About 0.10% to About 1.00%
Silicon (Si) is an essential element that functions as a deoxidizing agent in the steel making process. The deoxidizing effect is noticeable at a Si content of at least about 0.10%. However, a Si content exceeding about 1.00% decreases toughness and hot workability. Thus, the upper limit of the Si content is preferably about 1.00%. More preferably, the Si content is in the range of about 0.10% to about 0.50%.
Mn: About 0.05% to About 2.00%
Manganese (Mn) is an essential element that ensures strength of the martensitic stainless steel seamless pipe. The desired strength is achieved at an Mn content of at least about 0.05%. However, an Mn content exceeding about 2.00% decreases toughness. Thus, the C content is preferably in the range of about 0.05% to about 2.00% and more preferably about 0.30% to about 1.60%.
P: About 0.03% or Less
Phosphorus (P) is an element that causes a decrease in corrosion resistance, sulfide stress cracking resistance, and hot workability; the P content is preferably as low as possible. However, an extreme reduction in P content leads to a significant increase in process costs. Thus, the P content is about 0.03% or less in the invention in view of the balance between production costs and mechanical properties, i.e., corrosion resistance and sulfide stress cracking resistance.
S: About 0.005% or Less
Sulfur (S) is an element that causes a noticeable decrease in hot workability. The P content is preferably as low as possible for improving pipe productivity and improving toughness and stress corrosion cracking resistance. However, an extreme reduction in S content leads to a significant increase in process costs. Thus, the S content is about 0.010% or less and more preferably about 0.005% or less in the invention in view of pipe production by a general process.
Cr: About 10.0% to About 15.0%
Chromium (Cr) is a primary element that ensures high corrosion resistance and stress corrosion cracking resistance of the martensitic stainless steel seamless pipe. The desired corrosion resistance is achieved at a Cr content of at least about 10.0%. However, a Cr content exceeding about 15.0% causes deterioration of hot workability. Thus, the Cr content is preferably in the range of about 10.0% to about 15.0%.
Al: About 0.001% to About 0.05%
Aluminum (Al) is an element that functions as a strong deoxidizing agent in the steel making process. The deoxidizing effect is noticeable at an Al content of at least about 0.001%. However, an Al content exceeding about 0.05% leads to an increase in oxide inclusions, which decrease toughness. Thus, the upper limit of the Al content is about 0.05%.
The composition may further contain at least one element of Ni, Mo, and Cu; at least one element of Nb, V, Ti, Zr, B, and N; and/or at least one element of Ca and REM (rare earth metals).
At Least One Element of About 7.0% or Less of Ni, About 3.0% or Less of Mo and About 3.0% or Less of Cu
Ni, Mo, and Cu improve corrosion resistance of the pipe and may be added if necessary.
Ni significantly improves strength and toughness of the pipe, in addition to the corrosion resistance. These effects are noticeable at a Ni content of about 1.0% or more. However, these effects are not comparable with the Ni content if the Ni content exceeds about 7.0%.
Mo increases corrosion resistance and particularly pitting corrosion resistance. This effect is noticeable at a Mo content of about 0.1% or less. However, if the Mo content exceeds about 3.0% leads to a decrease in corrosion resistance, stress corrosion cracking resistance, and hot workability due to the formation of γ-ferrite.
Cu contributes to the formation of a stiff protective film, which increases corrosion resistance. This effect is noticeable at a Cu content of about 0.1% or more. However, a Cu content exceeding about 3.0% causes a decrease in hot workability.
At Least One Element of About 0.2% or Less of Nb, About 0.2% or Less of V, About 0.3% or Less of Ti, About 0.2% or Less of Zr, About 0.0005% to About 0.01% B, and About 0.07% or Less of N
Nb, V, Ti, Zr, B, and N improve mechanical strength such as toughness and may be added to the raw material, if necessary. However, if the raw material contains not less than about 0.2% Nb, not less than about 0.2% V, not less than about 0.3% Ti, not less than about 0.2% Zr, not less than about 0.01% B, or not less than about 0.07% N, the toughness and corrosion resistance decrease.
At Least One Element of About 0.0005% to About 0.01% Ca and About 0.0005% to About 0.01% REM (Rare Earth Metals)
Ca and REM contribute to spheroidization of inclusions. Preferably, the Ca content is at least about 0.0005% or the REM content is at least about 0.0005% for the spheroidization. However, a Ca content exceeding about 0.01% or an REM content exceeding about 0.01% decreases toughness and corrosion resistance.
The balance of the composition is composed of Fe and incidental impurities.
A martensitic stainless steel molten metal having the above composition is prepared in the invention by a known process using a converter or the like. Preferably, the molten metal is cast into slabs by a continuous casting process, and the slabs are rolled to form billets (raw materials for making original pipes). Alternatively, the molten metal is preferably cast into billets directly by a continuous casting process.
FIG. 2 shows outline of the production process according to selected aspects of the invention. A billet of the martensitic stainless steel having the above composition is heated to an austenitic temperature range and subjected to piercing and elongation to form an original pipe (original pipe production step).
Preferably, the austenitic temperature range is between about 1,100° C. and about 1,300° C. A temperature below about 1,100° C. causes unsuccessful piercing and elongation due to high deformation resistance. A temperature above about 1,300° C. causes a significant decrease in hot workability and toughness due to the formation of γ-ferrite, and a decrease in yield and an unsatisfactory surface state due to significant scaling.
Piercing may be performed by any known piercing mills of a skew rolling type (Mannesmann type) or press piercing type, without limitation. The pierced raw material is subjected to elongation to form an original pipe. The elongation may be performed with any known mill, such as, for example, a mandrel mill and a plug mill without limitation. Preferably, the elongation is completed at a temperature above about 800° C.
After elongation, the original pipe is cooled to the martensitic transforming temperature (Ms temperature) to form a structure substantially composed of martensite in the original pipe. The term “structure substantially composed of martensite” means that the structure of the cooled original pipe is composed of at least about 90% by area of martensitic phase. The balance is composed of about 10% or less of austenitic phase and about 2% or less of ferritic phase. This martensitic structure facilitates formation of a recrystallized microstructure during the subsequent reheating step. If the main phase is a phase other than the martensitic phase, the recrystallized microstructure is not formed during the reheating step. As a result, toughness is not so significantly improved or the toughness exhibits noticeable anisotropy.
In the finishing rolling step, the initial rolling temperature T (° C.) is between about the Ac1 transformation point and about the Ac3 transformation point. A low initial rolling temperature T below the Ac1 transformation point results in insufficient recrystallization. Mechanical properties exhibit significant anisotropy due to remaining rolling texture. A high initial rolling temperature T above the Ac3 transformation point accelerates recrystallization after the rolling step. As a consequence, toughness is not improved due to the inhibited formation of a microstructure. Accordingly, the initial rolling temperature T (° C.) is set to the range of about the Ac1 transformation point to about the Ac3 transformation point.
Preferably, in the finishing rolling step, the reduction in area R is in the range of about 10% to about 90%, and the initial rolling temperature T and the reduction in area R satisfies relationship (1):

800≦T−0.625R≦850  (1)

wherein the reduction in area R (%) is the ratio of a decrement by rolling to the sectional area before rolling: 



  
    Reduction
    ⁢
    
       
    
    ⁢
    in
    ⁢
    
       
    
    ⁢
    area
    ⁢
    
       
    
    ⁢
    R
  
  =
  
     
    
      
        [
        
          
            {
            
              
                (
                
                  sectional
                  ⁢
                  
                     
                  
                  ⁢
                  area
                  ⁢
                  
                     
                  
                  ⁢
                  before
                  ⁢
                  
                     
                  
                  ⁢
                  rolling
                
                )
              
              -
              
                (
                
                  sectional
                  ⁢
                  
                     
                  
                  ⁢
                  area
                  ⁢
                  
                     
                  
                  ⁢
                  after
                  ⁢
                  
                     
                  
                  ⁢
                  rolling
                
                )
              
            
            }
          
          /
          
            (
            
              sectional
              ⁢
              
                 
              
              ⁢
              area
              ⁢
              
                 
              
              ⁢
              before
              ⁢
              
                 
              
              ⁢
              rolling
            
            )
          
        
        ]
      
      ⁢
      H100
    
  




At a reduction in area R of less than about 10%, strain generated during the rolling is small. The formation of a microstructure during the rolling is inhibited. Thus, the resulting pipe does not exhibit desired strength and toughness. At a reduction rate in area R exceeding about 90%, anisotropy is noticeable because of elongation of the structure. Accordingly, the reduction in area R during the finishing rolling step is in the range of about 10% to about 90% and more preferably about 30% to about 70%.
In addition, the initial rolling temperature T is preferably controlled according to the reduction in area R so that these two parameters satisfy relationship (1) in the finishing rolling step of the invention.
FIG. 1 is a graph showing the effects of the reduction in area R and the initial rolling temperature T in finishing rolling on the toughness of a martensitic stainless steel seamless pipe.
In region C, the initial rolling temperature T and the reduction in area R satisfy relationship (1) and the initial rolling temperature T lies between the Ac1 transformation point and the Ac3 transformation point. In region C, both the absorbed energy (E−40)L per unit area of the longitudinal direction (L direction) and the absorbed energy (E−40)C per unit area of the circumferential direction (C direction) are about 180 J/cm2 or more, and the ratio (E−40)C/(E−40)L is about 0.80 or more. Accordingly, the pipe exhibits high absorbed energy per unit area indicating high toughness and reduced anisotropy in toughness. In regions A and B wherein T−0.625R<800, the absorbed energy per unit area in the C direction decreases to less than about 180 J/cm2 and the ratio (E−40)C/(E−40)L decreases to less than about 0.80. This indicates large anisotropy. In region B in which the initial rolling temperature T is higher than the Ac1 transformation point, however, the absorbed energy per unit area in the C direction is about 90 J/cm2 or more, which is a sufficiently satisfactory level in practice. In regions D and E wherein 850<T−0.625R, the absorbed energy per unit area in the L direction and the absorbed energy per unit area in the C direction decrease to less than about 180 J/cm2. However, in region D in which the initial rolling temperature T is lower than the Ac3 transformation point, the absorbed energy per unit area in the L direction and the absorbed energy per unit area in the D direction are about 90 J/cm2 or more, which is a sufficiently satisfactory level in practice. In conclusion, in ranges in which the initial rolling temperature T lies between the Ac1 transformation point and the Ac3 transformation point, the absorbed energy per unit area in the L direction and the absorbed energy per unit area in the D direction are about 90 J/cm2 or more, which indicates sufficiently high toughness in practice.
Preferably, after the finishing rolling satisfying relationship (1), the pipe is cooled in air or cooled at a cooling rate that is larger than that of air cooling. During the subsequent tempering, a martensitic microstructure having low anisotropy is formed. As a result, the processed pipe (final pipe product) has high mechanical strength and small anisotropy.
Preferably, the finishing rolling step is performed using a tandem mill, for example, a hot stretching reducing mill or a sizing mill.
EXAMPLES
Each of martensitic stainless steel molten metals having a composition shown in Table 1 was prepared in a converter and cast into a slab by a continuous casting process. The slab was rolled to form a billet (material for an original pipe). The billet was subjected to piercing using a Mannesmann-type piercing mill and elongation using a mandrel mill to form an original pipe as shown in Table 2. After elongation, the original pipe was cooled to a temperature below the Ms point so that the composition of the pipe was substantially composed of a martensitic structure. A test piece was prepared from a part of the original pipe and the structure was observed with an optical microscope. In comparative examples, original pipes were reheated immediately after elongation, without cooling to the temperature below the Ms point.
Each original pipe was reheated to a temperature shown in Table 2 and subjected to finishing rolling under conditions shown in Table 2 using a hot stretching reducing mill to form a pipe product having a size shown in Table 2. Next, the pipe was cooled in air and tempered at a temperature shown in Table 2.
Test pieces were prepared along the longitudinal direction (L direction) of each pipe product, and the yield strength YS and tensile strength TS in the L direction were measured according to ASTM A370. The absorbed energy E−40 per unit area at −40° C. was measured by a Charpy impact test in the circumferential direction (C direction) and the L direction according to ASTM A370. Each test piece had a thickness of 5 mm (sub size), and both ends along the C direction of the test piece for the C direction test were corrected. The ratio (E−40)C/(E−40)L of the absorbed energy in the C direction to the L direction was calculated. These results are shown in Table 3.
Each pipe according to the invention had a high yield strength of 550 MPa or more and a high absorbed energy per unit area in the L direction (E−40)L of 180 J/cm2 or more. The ratio (E−40)C/(E−40)L of the absorbed energy in the C direction to the L direction was at least 0.80. Accordingly, each pipe according to invention exhibits high toughness and low anisotropy of toughness compared with a conventional example (Pipe 8) and comparative examples. Each pipe in the comparative examples exhibited low toughness in the L direction or in the C direction and high anisotropy indicated by a low ratio (E−40)C/(E−40)L of less than 0.80.










TABLE 1









Composition (mass percent)





























Ni, Mo,
N, Nb,

Ac1
Ac3
Ms


Steel
C
Si
Mn
P
S
Al
Cr
Cu
Ti, V
REM, Ca
° C.
° C.
° C.





A
0.20
0.26
0.44
0.017
0.002
0.001
13.0
Ni: 0.14
N: 0.03
—
810
920
380


B
0.19
0.35
0.65
0.019
0.001
0.023
12.8
Ni: 0.01
N: 0.02,
—
810
940
370











V: 0.05


C
0.20
0.24
0.76
0.013
0.001
0.002
13.0
Ni: 0.05
N: 0.02,
—
820
940
370











Nb: 0.03,











V: 0.03


D
0.03
0.15
0.50
0.014
0.001
0.002
13.1
Ni: 4.0,
N: 0.05,
Ca: 0.0012
650
855
220










Mo: 1.0
Nb: 0.02




















TABLE 2









Original pipe production step
Finishing rolling step






















Pipe



Initial
Re-








Heating
Cooling
Struc-
Pipe size
Re-
Finishing
duction

Pipe size

Tem-
Re-
























temp. of
Final
ture
OD *2
T *3
heating
Rolling
Rate
P
OD *2
T *3

pering
marks


Pipe
Steel
billet
temp.
*1
(mm)
(mm)
temp.
Temp.
(%)
*4
(mm)
(mm)
Cooling
Temp.
*5

























1
A
1,250° C.
50° C.
M + A
172
7.2
850° C.
830° C.
61.1
792
73.0
7.0
Air
720° C.
PI


2
A
1,250° C.
50° C.
M + A
172
7.2
870° C.
850° C.
61.1
812
73.0
7.0
Air
700° C.
PI


3
A
1,250° C.
50° C.
M + A
172
7.2
890° C.
870° C.
61.1
832
73.0
7.0
Air
700° C.
PI


4
A
1,250° C.
50° C.
M + A
172
7.2
920° C.
900° C.
61.1
862
73.0
7.0
Air
700° C.
PI


5
A
1,250° C.
50° C.
M + A
172
7.2
970° C.
950° C.
61.1
912
73.0
7.0
Air
700° C.
CE


6
A
1,330° C.
50° C.
M + A +
172
7.2
870° C.
850° C.
61.1
812
73.0
7.0
Air
720° C.
CE






F *6


7
A
1,250° C.
400° C.
A
172
7.2
870° C.
850° C.
61.1
812
73.0
7.0
Air
720° C.
CE


8
A
1,250° C.
750° C.
A
172
7.2
970° C.
950° C.
61.1
912
73.0
7.0
Air
720° C.
TE


9
A
1,250° C.
50° C.
M + A
110
10.0
850° C.
830° C.
80.5
780
33.2
7.6
Air
720° C.
PI


10
A
1,250° C.
50° C.
M + A
110
10.0
890° C.
870° C.
80.5
820
33.2
7.6
Air
700° C.
PI


11
B
1,250° C.
50° C.
M + A
172
7.0
820° C.
800° C.
35.8
778
114.3
6.9
Air
700° C.
CE


12
B
1,250° C.
50° C.
M + A
172
7.0
870° C.
850° C.
35.8
828
114.3
6.9
Air
700° C.
PI


13
B
1,250° C.
50° C.
M + A
172
7.0
910° C.
890° C.
35.8
868
114.3
6.9
Air
700° C.
PI


14
B
1,250° C.
50° C.
M + A
192
8.9
800° C.
780° C.
13.0
772
168.2
8.9
Air
720° C.
CE


15
B
1,250° C.
50° C.
M + A
192
8.9
840° C.
820° C.
13.0
812
168.2
8.9
Air
720° C.
PI


16
B
1,250° C.
50° C.
M + A
192
8.9
870° C.
850° C.
13.0
842
168.2
8.9
Air
720° C.
PI


17
B
1,250° C.
50° C.
M + A
192
8.9
890° C.
870° C.
13.0
862
168.2
8.9
Air
700° C.
PI


18
D
1,250° C.
50° C.
M + A
192
8.9
840° C.
820° C.
13.0
812
168.2
8.9
Air
720° C.
PI


19
D
1,250° C.
50° C.
M + A
192
8.9
650° C.
630° C.
13.0
622
168.2
8.9
Air
640° C.
CE


20
A
1,250° C.
50° C.
M + A
110
10.0
970° C.
950° C.
80.5
900
33.2
7.6
Air
700° C.
CE


21
A
1,250° C.
50° C.
M + A
172
7.2
770° C.
750° C.
61.1
712
73.0
7.0
Air
720° C.
CE


22
B
1,250° C.
50° C.
M + A
172
7.0
770° C.
750° C.
35.8
728
114.3
6.9
Air
720° C.
CE


23
B
1,250° C.
50° C.
M + A
172
7.0
970° C.
950° C.
35.8
928
114.3
6.9
Air
700° C.
CE


24
B
1,250° C.
50° C.
M + A
192
8.9
770° C.
750° C.
13.0
742
168.2
8.9
Air
720° C.
CE


25
C
1,250° C.
50° C.
M + A
172
7.2
890° C.
870° C.
61.1
832
73.0
7.0
Air
700° C.
PI





*1 Crystal structure of the composition of original pipe, M = martensite, A = austenite, F = ferrite 


*2 OD = outer diameter, 


*3 T = thickness 


*4 parameter (center in relationship (1) = T − 0.625R) 


*5 PI = present invention, CE = comparative example, TE = conventional example 


*6 F content = 4% 
















TABLE 3









Toughness












Tensile Properties
Absorbed energy (J/mm2)














Pipe
YS (MPa)
TS (MPa)
L direction
C direction
Ratio C/L
Remarks
















1
601
769
241
116
0.48
Present Invention


2
593
763
230
205
0.89
Present Invention


3
623
783
208
195
0.94
Present Invention


4
599
769
128
106
0.83
Present Invention


5
587
760
96
89
0.93
Comparative example


6
573
764
73
65
0.89
Comparative example


7
600
774
221
96
0.43
Comparative example


8
572
760
78
72
0.92
Conventional Example


9
621
790
249
108
0.43
Present Invention


10
618
792
219
198
0.90
Present Invention


11
605
773
229
85
0.37
Comparative example


12
598
767
208
185
0.89
Present Invention


13
620
798
121
109
0.90
Present Invention


14
612
779
227
90
0.40
Comparative example


15
589
762
210
183
0.87
Present Invention


16
608
785
196
186
0.95
Present Invention


17
592
763
108
93
0.86
Present Invention


18
639
795
251
221
0.88
Present Invention


19
702
873
248
85
0.34
Comparative example


20
584
775
79
75
0.95
Comparative example


21
612
793
203
76
0.37
Comparative example


22
599
753
189
82
0.43
Comparative example


23
604
755
86
82
0.95
Comparative example


24
586
754
221
75
0.34
Comparative example


25
723
901
219
196
0.89
Present Invention

## Claims

1. A method for making a high-strength high-toughness martensitic stainless steel seamless pipe comprising:
heating a martensitic stainless steel raw material to an austenitic range; 
piercing and elongating the raw material to form an original pipe; 
cooling the original pipe to form a structure substantially composed of martensite in the original pipe; 
reheating the original pipe to a temperature in a dual-phase range between the Ac1 transformation point and the Ac3 transformation point directly after cooling the original pipe to form the structure substantially composed of martensite; 
finish-rolling the original pipe at an initial rolling temperature T (° C.) between the Ac1 transformation point and the Ac3 transformation point; 
cooling the original pipe to form a processed pipe having a predetermined size; and 
tempering the processed pipe at a temperature below the Ac1 transformation point.

2. The method according to claim 1, wherein a reduction in area R during finishing rolling is in the range of about 10% to about 90%, and the initial rolling temperature T and the reduction in area R satisfy the relationship: 800≦T−0.625R≦850.

3. The method of claim 1, wherein the raw material contains about 0.005% by weight to about 0.30% C, about 0.10% to about 1.00% Si, about 0.05% to about 2.00% Mn, about 0.03% or less of P, about 0.005% or less of S, about 10.0% to about 15.0% Cr, about 0.001% to about 0.05% Al; and the balance Fe and incidental impurities.

4. The method of claim 3, wherein the raw material further contains about 7.0% or less of Ni, about 3.0% or less of Mo, and about 3.0% or less of Cu; at least one element of about 0.2% or less of Nb, about 0.2% or less of V, about 0.3% or less of Ti, about 0.2% or less of Zr, about 0.0005% to about 0.01% B, and about 0.07% or less of N; about 0.0005% to about 0.01% Ca and about 0.0005% to about 0.01% REM (rare earth metals).

5. The method of claim 1, wherein the austenitic temperature is between about 1100° C. and about 1300° C.

6. The method of claim 1, wherein elongating the raw material is performed at a temperature of above about 800° C.

7. The method of claim 1, wherein the AC1 transformation point is at about 815° C.

8. The method of claim 1, wherein the AC3 transformation point is at about 920° C.

9. The method of claim 1, wherein a reduction in area R during finish rolling is between about 30% and about 70%.

10. The method of claim 1, wherein the steel has an absorbed energy (E−40)L per unit area of a longitudinal direction (L direction) and an absorbed energy (E−40)C per unit area of a circumferential direction (C direction) of about 180 J/cm2 or more.

11. The method of claim 1, wherein the steel has an absorbed energy (E−40)L per unit area of a longitudinal direction (L direction) and an adsorbed energy (E−40)L per unit area of a circumferential direction (C direction) of about 90 J/cm2 or more.

12. A method for making a high-strength high-toughness martensitic stainless steel seamless pipe comprising:
heating a martensitic stainless steel raw material to an austenitic range; 
piercing and elongating the raw material to form an original pipe; 
cooling the original pipe to form a structure substantially composed of martensite in the original pipe; 
reheating the original pipe to a temperature in a dual-phase range between the Ac1 transformation point and the Ac3 transformation point directly after cooling the original pipe to form the structure substantially composed of martensite; 
finish-rolling the original pipe at an initial rolling temperature T (° C.) between the Ac1 transformation point and the Ac3 transformation point; 
cooling the original pipe to form a processed pipe having a predetermined size; and 
tempering the processed pipe at a temperature below the Ac1 transformation point such that the steel has an absorbed energy (E−40)L per unit area of a longitudinal direction (L direction) and an absorbed energy (E−40)C per unit area of a circumferential direction (C direction) of about 180 J/cm2 or more, and 
a ratio (E−40)C/(E−40)L of about 8.0 or more.

13. A method for making a high-strength high-toughness martensitic stainless steel seamless pipe consisting essentially of:
heating a martensitic stainless steel raw material to an austenitic range; 
piercing and elongating the raw material to form an original pipe: 
cooling the original pipe to form a structure substantially composed of martensite in the original pipe; 
reheating the original pipe to a temperature in a dual-phase range between the Ac1 transformation point and the Ac3 transformation point; 
finish-rolling the original pipe at an initial rolling temperature T (° C.) between the Ac1 transformation point and the Ac3 transformation point; 
cooling the original pipe to form a processed pipe having a predetermined size; and 
tempering the processed pipe at a temperature below the Ac1 transformation point.