GB2066847A - Ferritic Stainless Steel - Google Patents

Ferritic Stainless Steel Download PDF

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GB2066847A
GB2066847A GB8011018A GB8011018A GB2066847A GB 2066847 A GB2066847 A GB 2066847A GB 8011018 A GB8011018 A GB 8011018A GB 8011018 A GB8011018 A GB 8011018A GB 2066847 A GB2066847 A GB 2066847A
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stainless steel
ferritic stainless
heats
titanium
nitrogen
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Allegheny Ludlum Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Arc Welding In General (AREA)
  • Catalysts (AREA)
  • Rolling Contact Bearings (AREA)
  • Load-Engaging Elements For Cranes (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

A ferritic stainless steel characterized by superior toughness both prior to and after welding, and by superior crevice and integranular corrosion resistance consists of, by weight, up to 0.08% carbon, up to 0.06% nitrogen, from 25.000 to 35.00% chromium, from 3.60 to 5.60% molybdenum, up to 2.00% manganese, from 2.00 to 5.00% nickel, up to 2.00% silicon, up to 0.5% aluminum, up to 2.00% titanium, zirconium and/or niobium, balance essentially iron. The sum of carbon plus nitrogen is in excess of 0.0275%. Titanium, zirconium and niobium are in accordance with the following equation: %Ti/6+%Zr/7+%Nb/8>/=(%C+%N)

Description

SPECIFICATION Ferritic Stainless Steel The present invention relates to a ferritic stainless steel.
British Patent Application No. 11 020/80, filed concurrently herewith, describes a ferritic stainless steel which is characterized by superior crevice and intergranular corrosion resistance.
The steel of Application No. , is distinguishable from that of United States Patent Nos. 3,932,174 and 3,929,473 in that it has up to 2% by weight titanium, zirconium and/or columbium in accordance with the following equation: %TV6+%Zr/7+ /OCb/8 > %C+%N and a carbon plus nitrogen content in excess of 275 parts per million. Because of its higher carbon and nitrogen content, it can be melted and refined by less costly procedures than can the steels of United States Patent Nos. 3,932,174 and 3,929,473.
Through the present invention, there is provided a steel which is tougher than that of Application No.
The present invention provides a ferritic stainless steel consisting essentially of, by weight, up to 0.08% carbon, up to 0.06% nitrogen, from 25.00 to 35.00% chromium, from 3.60 to 5.60% molybdenum, up to 2.00% manganese, from 2.00 to 5.00% nickel, up to 2.00% silicon, up to 0.5% aluminium, up to 2.00% titanium, zirconium and/or columbium, balance essentially iron; said titanium, zirconium and columbium being in accordance with the following equation: %TV6+%Zr/7+%Cb/8z%C+%N the sum of said carbon plus said nitrogen being in excess of 0.0275%.
For the reasons noted hereinabove, the alloy of the present invention is clearly distinguishable from that of United States Patent Nos. 3,932,174 and 3,929,473. It is also distinguishable from that of United States Patent Nos. 4,119,765. The alloy of United States Patent No. 4,119,765 specifies a maximum molybdenum content below that for the present invention.
Another reference of interest is a paper entitled, "Ferritic Stainless Steel Corrosion Resistance and Economy". The paper was written by Remus A. Lula and appeared in the July 1976 issue of Metal Progress, pages 24-29. It does not disclose the ferritic stainless steel of the present invention.
Carbon and nitrogen are usually present in the steel of the present invention in respective amounts of at least 0.005% and 0.010%, with the sum being in excess of 0.0300%. Chromium and molybdenum are preferably present in respective amounts of 28.50 to 30.50% and 3.75 to 4.75%.
Manganese and silicon are each usually present in amounts of less than 1.00%. Aluminium which may be present for its effect as a deoxidizer is usually present in amounts of less than 0.1%.
Titanium, columbium and/or zirconium are added to improve the crevice and intergranular corrosion resistance of the alloy, which in a sense is a high carbon plus nitrogen version of United States Patent No. 3,929,473. It has been determined, that stabilizers can be added to high carbon and/or nitrogen versions of United States Patent No. 3,929,473, without destroying the toughness and/or weldability of the alloy. Although it is preferred to add at least 0.15% of titanium, insofar as the sole presence of columbium can adversely affect the weldability of the alloy, it is within the scope of the present invention to add the required amount of stabilizer as either titanium or columbium.
Columbium has a beneficial effect, in comparison with titanium, on the toughness of the alloy. A particular embodiment of the invention calls for at least 0.15% columbium and at least 0.15% titanium.
Titanium, columbium and zirconium are preferably present in amounts up to 1.00% in accordance with the following equation: %Ti/6+%Zr/7+%Cb/8=1 .0 to 4.0 (%C+%N) Nickel is added to the alloy of the present invention to enhance its toughness. It is added in amounts of from 2.00 to 5.00%, and preferably in amounts of from 3.00 to 4.50%.
The ferritic stainless steel of the present invention is particularly suitable for use as a welded article.
The following examples are illustrative of several aspects of the invention.
Ingots from twenty-four heats (Heats A through X) were heated to 1121 C (20500F), hot rolled to 3.175 mm. (0.125 inch) strip, annealed at temperatures of 1065 or 1121 0C (1950 or 20500F), cold rolled to about 1.57 mm (0.062 inch) strip and annealed at temperatures of 1065 or 1121 C (1950 or 2050"F). Hot rolled and cold rolled specimens were subsequently evaluated for toughness. Other specimens were TIG welded and then evaluated for toughness.
The chemistry of the heats appears hereinbelow in Table I.
Table I Composftion (wt /0) Heat C N Cr Mo Mn Ni Si Al Ti Cb Fe A 0.030 0.025 28.96 4.20 0.34 0.45 0.36 0.029 0.50 - Bal.
B 0.030 0.026 29.05 4.18 0.34 0.46 0.37 0.029 0.20 0.32 Bal.
C 0.031 0.025 28.96 4.06 0.36 0.45 0.29 0.027 0.09 0.45 Bal.
D 0.034 0.027 28.95 4.20 0.43 0.46 0.37 0.040 0.19 0.41 Bal.
E 0.035 0.026 28.75 4.20 0.40 0.47 0.45 0.025 0.20 0.42 Bal.
F 0.032 0.024 29.52 4.10 0.37 0.51 0.28 0.030 0.31 0.44 Bai.
G 0.013 0.018 29.00 4.00 0.35 4.00 0.37 0.023 0.31 - Bal.
H 0.027 0.018 29.00 4.00 0.35 4.15 0.36 0.026 0.31 - Bal.
I 0.029 0.018 29.00 4.00 0.35 4.16 0.36 0.029 0.60 - Bal.
J 0.025 0.020 28.74 3.90 0.35 4.00 0.36 0.037 - 0.37 Bal.
K 0.034 0.016 29.10 4.00 0.36 4.10 0.38 0.010 - 0.52 Bal.
L 0.032 0.018 29.10 4.00 0.35 4.10 0.39 0.014 0.20 0.38 Bal.
M 0.018 0.025 29.23 4.04 0.32 3.00 0.34 0.050 0.11 0.29 Bal.
N 0.021 0.021 29.08 4.05 0.32 3.01 0.34 0.046 0.20 0.28 Bal.
0 0.019 0.023 28.95 4.10 0.32 3.00 0.35 0.021 0.10 0.42 Bal.
P 0.021 0.024 28.81 4.10 0.31 3.05 0.34 0.043 0.20 0.42 Bal.
Q 0.022 0.020 29.47 4.04 0.33 3.03 0.32 0.017 - 0.43 Bal.
R 0.020 0.023 29.20 4.04 0.33 3.03 0.31 0.040 - 0.64 Bal.
S 0.025 0.023 28.94 3.91 0.34 3.91 0.34 0.051 0.12 0.29 Bal.
T 0.020 0.020 29.23 4.03 0.33 4.18 0.33 0.046 0.20 0.28 Bal.
U 0.017 0.020 29.15 4.04 0.30 4.00 0.28 0.055 0.12 0.43 Bal.
V 0.018 0.022 29.10 4.04 0.30 4.00 0.28 0.021 0.18 0.43 Bal.
W 0.022 0.021 28.94 3.94 0.33 4.08 0.35 0.037 - 0.44 Bal.
X 0.024 0.022 28.96 3.93 0.33 4.10 0.32 0.040 - 0.64 Bal.
Note that Heats A through F are outside the subject invention. They do not have a nickel content between 2.00 and 5.00%. The present invention is dependent upon a nickel content in excess of 2.00%.
Additional data pertaining to the chemistry of the heats appears hereinbelow in Table II.
Table II Heat %C+%N%T@/G+%Zr/7+Cb/8 A 0.055 0.083 B 0.056 0.073 C 0.056 0.071 D 0.061 0.083 E 0.061 0.086 F 0.056 0.107 G 0.031 0.052 H 0.045 0.052 0.047 0.100 J 0.045 0.046 K 0.050 0.065 L 0.050 0.081 M 0.043 0.054 N 0.042 0.068 0 0.042 0.069 P 0.045 0.086 Q 0.042 0.054 R 0.043 0.080 S 0.048 0.856 T 0.040 0.068 U 0.037 0.074 V 0.040 0.084 W 0.043 0.055 X 0.( 0.080 Toughness was evaluated by determining the transition temperature using subsize transverse Charpy V-notch specimens for hot rolled and annealed material (3.1 75x 10.00 mm (0.125x0.394 inch) specimens), cold rolled and annealed material (1.57x10.00 mm (0.062x0.394 inch) specimens), as welded material (1.57x10.00 mm (0.062x0.394 inch) specimens) and welded and annealed material (1.57x 10.00 mm (0.062x0.394 inch) (specimens). Transition temperature was based upon a 50% ductüe-50% brittle fracture appearance. The transition temperatures for the hot rolled and cold rolled specimens appears hereinbelow in Table III. Heats A through L were annealed at 1 0650C (1 9500F). The other heats were annealed at 1121 C (20500F).
Table III Transition Temperature C( F) Hot Rolled Cold Rolled andAnnealed andAnnealed Water Air Water Air Quenched Cooled Quenched Cooled Heat C ( F) C ( F) %C (%F) %C (%F) A 54 (130) 149 (300) 2 (35) 46 (115) B 49 (120) 127 (260) -29 (-20) 18 (65) C 43 (110) 110 (230) -12 (10) 10 (50) D 57 (135) 160 (320) 4 (40) 29 (85) E 60 (140) 160 (320) -12 (10) 29 (85) F 99 (210) 99 (210) 4 (40) 32 (90) G -37 (-35) - -118 (-180) -73 ( -100) H -43 (-46) -115 (-175) -73 (-100) | -15 (5) - -118 (-180) -68 (-90) J -84 (-120) - -123 (-190) -112 (-170) K -56 (-70) - -129 (-200) -76 (-105) L -40 (-40) - -115 (-175) -90 (-130) M 10 (50) 38 (100) -90 (-130) N 2 (35) 18 (65) -84 (-120) 0 -15 (5) 13 (55) -87 (-125) P -1 (30) 21 (70) -93 (-135) 0 -37 (-35) 16 (60) -101 (-150) R -9 (15) 16 (60) -109 (-165) S -27 (-35) -9 (15) -121 (185) T -32 (-25) -9 (15) -118 (-180) U -54 (-65) -23 (-10) -115 (-175) V -56 (-70) -32 (-25) -118 (-180) W -68 (-90) -32 (-25) -129 (-200) X -73 (-100) -32 (-26) 143 (-225) The transition temperatures for the as welded and welded and annealed specimens appears hereinbelow in Table IV.
Heats A through F were annealed at 1 0650C (1950 F) prior to welding. The other heats were annealed at 1121 C (20500 F). All heats were water quenched. Post weld anneals were 1 0650C (1 9500F) for Heats A through F and at 1121 C (20500F) for the other heats. All heats were water quenched after the post weld anneal.
Table IV Transition Temperature C ( F) As Welded Welded andAnnealed Heat C ( F) C ( F) A 43 (110) -1 (30) B 16 (60) 2 (35) C 32 (90) 4 (40) D 41 (105) -4 (25) E 68 (155) 4 (40) F 54 (130) 10 (50) G -76 (-105) -76 (-105) H -62 (-80) -71 (-95) I -43 (-45) -71 (-215) J -79 (-110) -137 (-155) K -68 (-90) -104 (-120) L -51 (-60) -84 M -51 (-60) -54 (-65) Table IV (conrd) Transition Temperature C ( F) As Welded Welded and Annealed Heat C ( F) C ( F) N -18 (0) -40 (-40) O -29 (-20) -65 (-85) P -23 (-10) -59 (-75) Q -51 (-60) -79 (-110) R -29 (-20) -59 (-75) S -40 (-40) -93 (-135) T -51 (-60) -73 (-100) U -79 (-100) -104 (-115) V -82 (-115) -84 (-120) W -73 (-100) -107 (-160) X -96 (-140) -129 (-200) The benefit of nickel is clearly evident from Tables 1H and IV. Heats G through X have substantially lower transition temperatures, and are therefore substantially tougher than are Heats A through F.
Significantly, Heats G through X are within the present invention whereas Heats A through F are not.
Heats G through X having in excess of 2.00% nickel.
The lower transition temperatures for Heats G through X is exemplified hereinbelow in Table V which is a composite of Tables III and IV.
Table V Transition Tempereture C ( F) Heats A-F Heats G-X Hot Rolled and Annealed (WaterQuenched) 43 (110) to 99 (210) -84 (-120) to 10 (50) Hot Rolled and Annealed (Air Cooled) 99 (210) to 160 (320) -32 (-25) to 38 (100) Cold Rolled and Annealed (Water Quenched) -29 (-20) to 4 (40) -143 (-225) to -84 (-120) Cold Rolled and Annealed (Air Cooled) 10(60) to 46 (115) -112 (-170) to -68 (-90) As Welded 16(60) to 68 (155) -96(-140) to -18(0) Welded and Annealed -4(25) to 10 (50) -137 (-215) to -40 (-40) Note that in every instance the maximum transition temperature for Heats G through X is lower than the minimum transition temperature for Heats A through F. The data clearly shows that Heats G through X are tougher than are Heats A through F.
Additional specimens of Heats G through X were evaluated for crevice and intergranular corrosion resistance. These specimens were prepared as were the specimens referred to hereinbelow.
Crevice corrosion resistance was evaluated by immersing 25.4 mm. (1 inch) by 50.8 mm. (2 inch) surface ground specimens in a 10% ferric chloride solution for 72 hours. Testing was performed at a temperature of 500C (1220 F). Crevices were created by employing polytetrafluoroethylene biocks on the front and back, held in position by pairs of rubber bands stretched at 900 to one another in both longitudinal and transverse directions. The test is described in Designation: G 48-76 of the America Society for Testing And Materials.
The results of the evaluation appear hereinbelow in Table VI. Specimens were in the cold rolled and annealed condition, in the as welded condition and in the as welded and annealed condition.
Table VI 10% Ferric Chloride Crevice Corrosion Test Weight Loss (Grams) Cold Rolled Welded Heat andAnnealed As Welded andAnnealed* G - 0.0001 0.0008 H - 0.1588 0.0005 I - 0.0 0.0004 J - 0.0 0.0001 K - 0.0 0.0015 L - 0.0001 0.0001 M 0.0 0.0004 0.0003 Table VI (conrd) 10% Ferric Chloride Crevice Corrosion Test Weight Loss (Grams) Cold Rolled Welden Heat andAnnealed As Welded andAnnealed* N 0.0009 0.0027 0.0009 0 0.0 0.0007 0.0001 P 0.0001 0.0004 0.0004 Ct 0.0 0.0005 0.0039 R 0.0007 0.0032 0.0068 S 0.0056 0.0007 0.0 T 0.0 0.0001 0.0056 U 0.0002 0.0001 0.0 V 0.0001 0.0078 0.0002 W 0.0001 0.0 0.0063 X 0.0 0.0003 0.0060 * Anncaled at 1121 C (2050 F) - Water Quenched.
From Table VI, it is noted that the crevice corrosion resistance of Heats G through X is excellent.
The alloy of the present invention is indeed characterized by superior crevice corrosion resistance.
Intergranular corrosion resistance was evaluated by immersing 25.4 mm. (1 inch) by 50.8 mm. (2 inch) surface ground specimens in a boiling cupric sulfate50% sulfuric acid solution for 120 hours.
The usuai pass-fail criteria for this test are a corrosion rate of 0.6 mm. (24.0 mils) per year (0.05 mm.
(0.0020 inches) per month) and a satisfactory microscopic examination. This test is recommended for stabilized high chromium ferritic stainless steels.
The results of the evaluation appear hereinbelow in Table VII. Specimens were in the as welded condition and in the as welded and annealed condition.
Table VII Cupric Sulfate-50% Sulfuric Acid Corrosion Test Microscopic Examination Corrosion Rate (mm (inches) per month) (at (30X) As Welded Welded andAnnealed* Welded and Heat (mm) (inches) (mm) (inches) As Welded Annealed* G 0.012373 (0.000495) 0.016078 (0.000633) NA** NA H 0.016408 (0.000646) 0.014783 (0.000582) NA NA 0.012903 (0.000508) 0.017170 (0.000676) NA NA J 0.011049 (0.000435) 0.016027 (0.000631) NA NA K 0.009347 (0.000368) 0.018669 (0.000735) NA NA L 0.009601 (0.000378) 0.015113 (0.000595) NA NA S 0.012725 (0.000501) 0.015799 (0.000622) NA NA T 0.011913 (0.000469) 0.012649 (0.000498) NA NA U 0.010185 (0.000401) 0.016027 (0.000631) NA NA V 0.012217 (0.000481) 0.012319 (0.000485) NA NA W 0.012217 (0.000481) 0.012827 (0.000505) NA NA X 0,012903 (0.000508) 0.013843 (0.000545) NA NA *Annealed at 1 C (20500F)-WaterQuenched **NA: No Intergranular Attack or Grain Dropping From Table VII. it is noted that Heats G through L and S through X exhibit superior intergranular corrosion resistance. Each specimen passed the test.

Claims (10)

Claims
1 . A ferritic stainless steel consisting essentially of, by weight, up to 0.08% carbon, up to 0.06% nitrogen, from 25.00 to 35.00% Chromium, from 3.60 to 5.60% molybdenum, up to 2.00% manganese, from 2.00 to 5.00% nickel, up to 2.00% silicon, up to 0.5% aluminium, up to 2.00% titanium, zirconium and/or columbium, balance essentially iron; said titanium, zirconium and columbium being in accordance with the following equation: %TV6+%Zr/7+%Cb/8#%C+%N the sum of said carbon plus said nitrogen being in excess of 0.0275%.
2. A ferritic stainless steel according to claim 1, having from 3.00 to 4.50% nickel.
3. A ferritic stainless steel according to claim 1 or 2, having at least 0.005% carbon and at least 0.010% nitrogen, the sum of said carbon plus said nitrogen being in excess of 0.0300%.
4. A ferritic stainless steel according to claim 1,2 or 3, having from 28.50 to 30.50% chromium.
5. A ferritic stainless steel according to any one of the preceding claims, having from 3.75 to 4.75% molybdenum.
6. A ferritic stainless steel according to any one of the preceding claims, having up to 1.00% titanium, zirconium and/or columbium in accordance with the following equation: %Ti/6+%Zr/7+%Cb/8=1.0 to 4.0 (%C+%N)
7. A ferritic stainless steel according to any one of the preceding claims, having at least 0.1 5% titanium.
8. A ferritic stainless steel according to claim 7, having at least 0.1 5% columbium.
9. A ferritic stainless steel according to any one of the preceding claims, having at least 0.005% carbon, at least 0.010% nitrogen, from 28.50 to 30.50% chromium, from 3.75 to 4.75% molybdenum, from 3.00 to 4.50% nickel, and up to 1.00% titanium, zirconium and/or columbium in accordance with the following equation: %TI/6+%Zr/7+Cb/8=1.0 to 4.0 (%C+%N) the sum of said carbon plus said nitrogen being in excess of 0.0300%.
10. A ferritic stainless steel substantially according to any one of the specific Examples of Heats G to X herein.
GB8011018A 1980-01-03 1980-04-02 Ferritic stainless steel Expired GB2066847B (en)

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Cited By (1)

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Publication number Priority date Publication date Assignee Title
GB2193726A (en) * 1986-07-23 1988-02-17 Jgc Corp Carbon containing compound treating apparatus with resistance to carbon deposition

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SE453838B (en) * 1985-09-05 1988-03-07 Santrade Ltd HIGH-QUALITY FERRIT-AUSTENITIC STAINLESS STEEL
JPH0422870U (en) * 1990-06-11 1992-02-25

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CA922543A (en) * 1969-07-11 1973-03-13 The International Nickel Company Of Canada Corrosion resistant ferritic stainless steel
FR2091642A5 (en) * 1970-05-16 1972-01-14 Nippon Steel Corp Stainless steel resistant to pitting corrosion -and suitable for comp - used in sewater
GB1359629A (en) * 1971-10-26 1974-07-10 Deutsche Edelstahlwerke Gmbh Corrosion-resistant ferritic chrome steel
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Cited By (2)

* Cited by examiner, † Cited by third party
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GB2193726A (en) * 1986-07-23 1988-02-17 Jgc Corp Carbon containing compound treating apparatus with resistance to carbon deposition
GB2193726B (en) * 1986-07-23 1991-05-22 Jgc Corp Carbon containing compound treating apparatus with resistance to carbon deposition

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NO155351C (en) 1987-03-18
BR8001877A (en) 1981-07-14
GB2066847B (en) 1984-08-08
KR850000980B1 (en) 1985-07-05
JPH0321624B2 (en) 1991-03-25
BE882793A (en) 1980-10-15
FR2473068A1 (en) 1981-07-10
PL226697A1 (en) 1981-08-07
AT376707B (en) 1984-12-27
MX6596E (en) 1985-08-14
AU535783B2 (en) 1984-04-05
SE436576C (en) 1987-03-16
DE3011048A1 (en) 1981-07-23
PL124420B1 (en) 1983-01-31

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