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Previous Issue: New Next Planned Update: TBD Page 1 of 40 Primary contacts: Lobley, Graham R. on 966-3-8746678; Niemeyer, Dennis C. on 966-3-8736700
Copyright©Saudi Aramco 2008. All rights reserved.
Best Practice
SABP-A-022 25 August 2008 Stainless Steel Fabrication, Testing and Installation
Document Responsibility: Materials & Corrosion Control Standards Committee
Saudi Aramco DeskTop Standards Table of Contents 1 Scope and Purpose............................................ 2 2 Conflicts and Deviations..................................... 2 3 References......................................................... 2 4 Definitions and Abbreviations............................. 5 5 Introduction to Stainless Steels.......................... 6 6 Classes of Stainless Steel.................................. 6 7 Composition, Corrosion Resistance and Sensitization..................................... 9 8 Materials Selection........................................... 11 9 Castings .......................................................... 12 10 Fabrication....................................................... 13 10.1 Welding and Corrosion Resistance....... 13 10.2 Welding of Stainless Steels................... 14 10.3 Storage.................................................. 32 10.4 Shop Fabrication................................... 32 10.5 Pickling, Passivation & Iron Removal.... 33 10.6 Field Fabrication.................................... 34 11 Hydrostatic Testing.......................................... 36 12 Microbiologically Influenced Corrosion (MIC)... 37 13 Coating Stainless Steel.................................... 38 14 Summary.......................................................... 39
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
Issue Date: 25 August 2008
Next Planned Update: TBD Stainless Steel Fabrication, Testing and Installation
Page 2 of 40
1 Scope and Purpose
Stainless steels are more expensive than carbon and low alloy steels and are normally
selected for their superior corrosion or heat resistance. For the austenitic stainless
steels, good low temperature toughness is also a key mechanical property. However,
improper fabrication and testing procedures can seriously degrade corrosion resistance
and directly lead to premature failures.
This SABP provides guidelines to optimize performance of stainless steels, particularly
austenitic, duplex and martensitic grades. It identifies specific procedures and
specifications to be followed, during manufacturing, fabrication and commissioning, in
order to achieve optimum performance of stainless steel equipment and piping.
This SABP is based on current industry experiences and is intended for internal Saudi
Aramco operations and maintenance applications. It also provides guidance for
inspection in fabrication facilities.
2 Conflicts and Deviations
If there is a conflict between this Best Practice and a Saudi Aramco standard then the
Standard shall govern. If there is a conflict between this Best Practice and an approved
welding procedure then the approved welding procedure shall govern. If there is a
conflict between this Best Practice and other standards and specifications, please
contact the Coordinator of ME&CCD/CSD.
3 References
3.1 Saudi Aramco References
Saudi Aramco Engineering Standards
SAES-A-007 Hydrostatic Testing Fluids and Lay-Up
Procedures
SAES-G-005 Centrifugal Pumps
SAES-H-001 Coating Selection & Application Requirements for
Industrial Plants and Equipment
SAES-L-132 Material Selection for Piping Systems
SAES-W-010 Welding Requirements for Pressure Vessels
SAES-W-011 Welding Requirements for On-Plot Piping
SAES-W-014 Weld Overlays and welding of Clad Materials
SAES-W-016 Welding of Special Corrosion Resistant Materials
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
Issue Date: 25 August 2008
Next Planned Update: TBD Stainless Steel Fabrication, Testing and Installation
Page 3 of 40
Saudi Aramco Standard Drawing
AD-036821 Material Guide for Centrifugal Pumps
Saudi Aramco Best Practice
SABP-A-001 Polythionic Acid SCC Mitigation - Materials
Selection and Effective Protection of Austenitic
Stainless Steels and other Austenitic Alloys
Saudi Aramco Technical Alert
ALERT-93-011 Technical Alert Number 11, Avesta 254SMO
Stainless, issued 11/21/93
3.2 Industry Codes and Standards
American Petroleum Institute
API TR 938-C Use of Duplex Stainless Steels in the Oil Refining
Industry-First Edition, 2005
American Society for Testing and Materials
ASTM A380 Standard Practice for Cleaning, Descaling and
Passivation of Stainless Steel Parts, Equipment,
and Systems
ASTM A967 Standard Specification for Chemical Passivation
Treatments for Stainless Steel Parts
ASTM C871 Standard Test Methods for Chemical Analysis of
Thermal Insulation Materials for Leachable
Chloride, Fluoride, Silicate, and Sodium Ions
American Welding Society
AWS D10.18:2008 Guide for Welding Ferritic/Austenitic Duplex
Stainless Steel Piping and Tubing
AWS D18.2:1999 Guide to Weld Discoloration Levels on Inside of
Austenitic Stainless Steel Tube
International Standards Organization
ISO 15156-3 Petroleum, Petrochemical and Natural Gas
Industries Materials for Use in H2S-Containing
Environments in Oil and Gas Production Part
3: Cracking-Resistant CRAs (Corrosion-
Resistant Alloys) and Other Alloys
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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Next Planned Update: TBD Stainless Steel Fabrication, Testing and Installation
Page 4 of 40
National Association of Corrosion Engineers
NACE MR103-2007 Materials Resistant to Sulfide Stress Cracking in
Corrosive Petroleum Refining Environments
NACE RP0198 The Control of Corrosion Under Thermal
Insulation and Fireproofing Materials - A
Systems Approach
New Zealand Stainless Steel Development Association
NZSSDA Code of Practice for the Fabrication of Stainless
Steel Plant & Equipment, 2001
3.3 Publications
Optimising Stainless Steel Piping Fabrication Practice, Dr. Liane Smith, North
Scottish Branch of the Welding & Joining Society, Aberdeen, 26th
May 2005
NiDI Publication 11003: Nickel Stainless Steels for Marine Environments,
Natural Waters and Brines (1987)
Guidelines for Successful Use of Stainless Steel in Potable Water Treatment.
Plants (PWTP), R. E. Avery, S. Lamb, A. H. Tuthill, Nickel Development
Institute, April 1998
Fabricating Stainless Steels for the Water Industry Nickel Development Institute
Reference Book 11026, C. Powell, D. Jordan, October 2005
Microbiologically Influenced Corrosion – Case Studies in Australasia, ACCA
2007, Paper 21, L. H. Boulton
Influence of Sulfate-Reducing Bacteria on Corrosion of 2205-Type Duplex
Stainless Steel in Chloride Medium, ACCA 2007, Paper 72, P. J. Antony, R.K.
Singh Raman, et. al.
“Welding of Stainless Steels and other Joining Methods,” A Designers’
Handbook Series No. 9002, NiDI, Nickel Development Institute
American Welding Society, “AWS Welding Handbook, Eighth Edition Volume 4,
Materials and Applications Part 2”, 1998
ASM Handbook, Volume 6, “Welding, Brazing, and Soldering,” 1993
Stainless Steels, Properties, How to Weld Them, Where to Use Them, Kotecki,
D. and Armao, F., 2003, The Lincoln Electric Company
Welding of Austenitic Stainless Steels - a Guide to Best Practice, TWI Members
Website
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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4 Definitions and Abbreviations
API American Petroleum Institute
ASSDA Australian Stainless Steel Development Association
ASTM American Society for Testing & Materials
CRA Corrosion Resistant Alloy
CUI Corrosion under Insulation
DSS Duplex Stainless steel
Free Iron Surface contamination of SS with carbon or ferritic steels
HAZ Heat Affected Zone
ISO International Standards Organization
MIC Microbiologically Influenced Corrosion
NACE National Association of Corrosion Engineers
NZSSDA New Zealand Stainless Steel Development Association
PASCC SCC which can occur rapidly under refinery shutdown or T&I
conditions. Cracking is due to sulfur acids forming from sulfide scale,
air and moisture acting on sensitized austenitic stainless steels.
Phase Balance Percentage of delta ferrite in duplex stainless steel
PMI Positive Material Identification is a chemical analysis that ideally
includes all alloying elements, to determine conformance to specified
alloy composition. It can be used to check all parts, including weld
consumables and fabricated components.
PWHT Postweld heat treated: Solution Anneal and rapid cool
SCC Stress Corrosion Cracking
SDSS Superduplex Stainless Steel
Sensitization Formation of chromium carbides along grain boundaries which causes
loss in corrosion resistance. Sensitization is dependent on the
composition (see sections 9 and 10.2).
Stabilization Stabilization is an alloying method of preventing sensitization.
Stabilized grades with Ti (grade 321) or Nb (grade 347) are commonly
used. Ti and Nb additions preferentially combine with the carbon,
preventing the depletion in chromium.
SSC Sulfide Stress Cracking
SS Stainless Steel
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SSS Super Austenitic Stainless Steel
5 Introduction to Stainless Steels
Stainless steels are selected for service in oil, gas and downstream systems because of
their high level of corrosion resistance in typical producing and refinery environments.
The protective thin chromium-rich passive film forms spontaneously in the presence of
oxygen. Stainless steel grades are specified for ambient, cryogenic and high
temperature services.
The stainless steels addressed in this best practice (BP) are primarily the 300-series
austenitic stainless steels and the duplex stainless steels. Unfortunately, these materials
are not totally resistant to corrosion in other environmental conditions. In particular,
they are sensitive to pitting and crevice corrosion in aerated water environments with
chloride ions present at certain temperature conditions.
Stainless steel piping systems are typically hydrotested with water of varying quality
from potable water through to raw water with or without various chemicals present.
Depending upon the duration of exposure, any of these environments may result in
pitting attack. The resistance to pitting is strongly affected by the stability of the
protective passive film on the stainless steel, which is deleteriously affected in various
ways by welding. Microbes introduced in the hydrotest water can promote MIC as
another form of pitting. This usually occurs at weak points such as heat tint oxides, that
are associated with welding cycles.
Two approaches are therefore used for preventing pitting attack of stainless steels
during hydrotesting and prior to service. The fabricator should make every effort to
optimize the quality of the weld and minimize the reduction of passive film quality.
Also, the commissioning procedures should be optimized to minimize the corrosivity of
the environment for the hydrotest period.
The purpose of this BP is to provide guidance on optimum practice at every step in
order to give the very best confidence in the quality of fabrications, castings and other
products.
6 Classes of Stainless Steel
Stainless steels are broadly defined as steels that contain at least 11% Cr. On the basis
of microstructure, five major families of stainless steels are recognized: ferritic,
martensitic, austenitic, duplex and precipitation-hardenable (PH).
The simplified Alloy Tree (Figure 1) shows the relationship of these types of stainless,
building from a base case of 405 ferritic stainless steel (composition 11.5 – 14.5% Cr,
≤0.08% C). Adding C gives a martensitic structure, adding more Cr and > 8%Ni gives
an austenitic microstructure, adding less Ni and some Mo gives a duplex structure,
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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finally, adding Cr, Ni and Cu gives a precipitation hardening stainless steel. Austenitic
steels include 316 with Mo to increase pitting resistance, low C and weld stabilized
grades (with Ti [321] or Cb [347]). Higher %C and heat resisting grades are specified
for the highest temperatures, where creep and oxidation are the principal damage
mechanisms (examples 304H and 310).
Ferritic stainless steels are named because their body-centered-cubic (bcc) crystal
structure is the same as iron at room temperature. Their Cr content usually range from
11 to 18%. They are magnetic, have moderate corrosion resistance and are not
susceptible to SCC. Generally, ferritic stainless steels do not have particularly high
strength. Their annealed yield strengths range from 275 to 350 MPa (40 to 50 ksi), and
their poor toughness limits their fabricability and the usable section size
Martensitic stainless steels are similar to Fe-C alloys that are austenitized, hardened
by quenching, and then tempered for increased ductility and toughness. These alloys
are strongly magnetic and their heat-treated structure is body-centered tetragonal. In the
annealed condition, they have a tensile yield strength of about 275 MPa (40 ksi) and are
generally machined, cold formed, and cold worked in this condition.
Austenitic stainless steels comprise the largest stainless family, in terms of number of
alloys and usage. Like the ferritic alloys, they cannot be hardened by heat treatment.
Austenitic alloys are nonmagnetic in the solution annealed condition. Castings, welds
and cold-worked austenitic materials can show appreciable magnetism, due to the
presence of second phases such as delta ferrite or martensite. The austenite structure is
face-centered-cubic (fcc), like the high-temperature (900 to 1400°C) austenite form of
iron. They possess excellent ductility, formability, and toughness, even at cryogenic
temperatures. In addition, they can be substantially hardened by cold work.
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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Figure 1 – Stainless Steel Alloy Tree
Austenitic stainless steels of the 300 series are the most commonly used, such as 304,
316, 321 and 347 grades (see Table 1). Higher Mn-containing alloys, with Mn
exceeding 4%, are covered under 200 series stainless steel specifications. Examples
used in rotating equipment include UNS S20910 (Nitronic 50) and UNS S21800
(Nitronic 60) for shafts, wear rings, etc. The higher Mn levels greatly improve
resistance to wear including galling (a common problem with 300 series steels).
Duplex stainless steels are Cr-Ni-Mo alloys that contain a balanced mixture of
austenite and ferrite, and are therefore significantly magnetic. Duplex stainless steels
combine the optimum properties of austenitic and ferritic types. Typically, they contain
18 - 26% Cr plus 4.5 to 6.5% Ni. Their duplex structure results in improved SCC
resistance, compared with the austenitic stainless steels and improved toughness and
ductility, compared with the ferritic stainless steels. They can have yield strengths
ranging from 550 to 690 MPa (80 to 100 ksi) in the annealed condition, which is
approximately twice the strength level of either phase alone. Typical applications
include handling chlorinated seawater and for some heat exchanger tubing.
Temperature limits typically range from -50 to +300ºC.
Duplex stainless steels have been utilized for seawater applications, such as in Seawater
Treatment Plants and some refinery heat exchanger tubing. Applications have been
limited by two factors: (1) weldability concerns due to formation of deleterious
Ferritic
405 base: 11 – 12% Cr
< 0.03 %C
Martensitic
410 base:
12 %Cr, 0.1 - 0.2%C
Austenitic
304 base:
18 %Cr, 8% Ni, 0.03 -0.08%C
Duplex
2205 base:
22%Cr, 5%Ni, 3%Mo, N
Precipitation
Hardening
15-5 PH 17-4 PH
316 (Mo-alloyed)
Stabilized (Ti or Cb)
or low C (≤ 0.03) Heat Resistant (310)
& high C grades
Austenitic
304 base:
18 %Cr, 8% Ni, 0.03 -0.08%C
13 Cr
13%Cr, 6%Ni, Mo
A486 CA6NM
Superduplex
PREN ⋝ 40
2507 & UNS S32760
2205 base:
22%Cr, 5%Ni, 3%Mo, N
Superaustenitic
PREN ⋝ 40
UNS S31254
0.03 -0.08%C
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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intermetallic phases leading to loss of toughness and corrosion resistance, especially
with the superduplex grades; (2) low-to-moderate resistance to SSC.
PH stainless steels may be martensitic, semi-austenitic or austenitic. They combine
the heat treatability of normal martensitic grades with the corrosion resistance of
austenitics. They are available in bar form for the production of heavy duty engineering
components. Various alloying elements, such as Al, Ti, Nb or Cu, are used to achieve
age hardening. They generally form intermetallic compounds, but in S17400 (17-4PH),
fine Cu precipitates are formed. Typical uses of 17-4PH include valve stems, drive
shafts and control valve parts.
“L”, Dual Certified and Stabilized Grades
Types 304L or 316L are the standard grades of stainless steel used for welded
applications. Type 316L with 2 - 3% Mo is more resistant to pitting and crevice
corrosion and is preferred over Type 304L for more severe services. The low C "L"
grade which has a maximum of 0.03% C is required for welded structures to minimize
risk of sensitization. Stabilized grades 321 and 347 are also specified for welded
structures.
Where mechanical strength is important for design purposes, the slightly lower tensile
and yield strengths of the "L" grades should be recognized. It is increasingly common
to encounter Dual Certified Type 304/304L and Type 316/316L stainless steel in
warehouse stock. Dual certification means that it meets the 0.03% C maximum
requirement for the "L" grades and also meets the higher mechanical properties of the
regular grades.
7 Composition, Corrosion Resistance and Sensitization
The resistance of stainless steels to pitting and crevice corrosion in aerated waters is
strongly related to the chemical composition. Steels with higher levels of chromium
(Cr), molybdenum (Mo) and nitrogen (N) are more resistant. The resistance to pitting is
related to the composition using the empirical Pitting Resistance Equivalent Number
(PREN) as follows:
PREN = %Cr + 3.3 x %Mo + 16 x %N
Generally, stainless steels with a PREN value above 40 are resistant to pitting corrosion
in ambient temperature seawater. These steels are sometimes referred to as
superstainless steels (SSSs). Superstainless cast and wrought grades are specified with
PREN ≥ 40 in SAES-G-005, Standard Drawing AD-036821 for highly corrosive
services, such as for pumps handling produced brine water, with high TDS and Cl
levels.
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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PREN data relates bulk chemistry to corrosion performance, but this is only a ranking
guideline to compare different alloys. ISO 15156-3 includes PREN ranges for stainless
steels in the austenitic and duplex alloy classes. The PREN does not factor alloy
microstructure, microsegregation or surface condition, all of which strongly influence
alloy performance in practice. Thermal history, including original heat treatment and
welding, are major factors influencing ultimate performance. Consequently, SSS
casting alloys must be in the solution annealed condition after weld repairs.
It is important to ensure that the grades of stainless steels which are used in piping
systems are not mixed up. A section of piping with lower resistance to pitting attack, as
a consequence of its lower PREN value, may be more likely to initiate pitting when
connected to higher alloyed stainless steel.
Weld metal must have a pitting resistance equivalent to or better than that of the parent
metal. This means that even in the root region, with some dilution of the filler metal
composition by the parent metal, the pitting resistance will still be acceptable. For this
reason, superstainless steels such as UNS S31254 are fusion welded using overalloyed
filler metal (Inconel 625). ALERT-93-011 (Saudi Aramco Technical Alert Number 11)
provides additional information and advice concerning seawater service, as follows:
Corrosion damage initiated in the root pass of the UNS S31254 butt-welds.
Field and laboratory investigations indicate the most likely cause of failure was
insufficient (or no) addition of the recommended Inconel 625 filler material during
welding of the root pass.
Table 1 – Some Commonly Used Stainless Steel Grades
Material Nominal Composition Example
Specification (ASTM/SAE)
UNS # / Grade
PREN
Ferritic – 400 series
11 Cr-C≤0.08 13 Cr-C≤0.08
A240 A240
S40500 S41008
10.5 – 12.5 11.5 – 14.5
Martensitic – 400 series
12 Cr 13Cr-4Ni-0.5Mo 13Cr-4Ni-0.5Mo
A240-410 A487 CA6NM A276
S41000 J91540 S41500
11.5 – 14.0 12.8 – 17.3 12.8 – 17.3
Austenitic - 300 series 200 series Superaustenitic
18Cr-9Ni 18Cr-8Ni-2.5Mo 18Cr-8Ni-3.5Mo 18Cr-10Ni-Ti 18Cr-10Ni-Nb 25Cr-20Ni 22Cr-12.5Ni-5Mn-2.5Mo-0.3N 17Cr-8.5Ni-8Mn-4Si-0.15N 20Cr-18Ni-6Mo-N (254SMO) 21Cr-24Ni-6Mo-N (AL-6XN)
A240 S30400 A240 S31600 A240 S31700 A240 S32100 A240 S34700 A240 S31000 A240 XM-19 A240 S21800 A240-S31254 B688
S30400 S31600 S31700 S32100 S34700 S31000 S20910 S21800 S31254 N08367
18 - 20 23 - 28 28 - 33 17 - 20 17 - 19 24 - 26 29 -38 17.3 - 20.9 42 - 45 43 – 49
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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Material Nominal Composition Example
Specification (ASTM/SAE)
UNS # / Grade
PREN
Other grades
20Cr-35Ni-2.5Mo-3.5Cu 21Cr-25Ni-4.5Mo-1.5Cu
B464 B673
N08020 (20Cb-3) N08904 (904L)
26 - 31 32 - 40
Duplex Superduplex
22Cr-5Ni-3.5Mo-N 25Cr-7Ni-3.5Mo-N-W 25Cr-7Ni-3.5Mo-N-W 25Cr-7Ni-4Mo-0.3N
A182-F51 A890 Gr 4A A276/A182-F55
A890 Gr 6A A240-S32750
S31803 S32205 J92205 S32760 J93380 S32750
31 - 38 40 - 46 39 - 46 38 - 44
Precipitation Hardening
17Cr-4Ni-3Cu A564 Type 630 S17400 15 – 17.5
Note: The international UNS numbering system uses a letter prefix and numbers to designate specific alloy
grades. In this system: S = a regular stainless steel, N = a Ni-based alloy (including some higher grade stainless steels) and J = a casting specification.
Autogenous welds in UNS S31254 (without Inconel 625 filler) lack sufficient
corrosion resistance to withstand seawater - particularly chlorinated seawater.
Therefore, welding must be performed with the continuous addition of filler.
Sensitization is the formation of chromium carbides along grain boundaries that causes
loss in corrosion resistance. The degree of sensitization is dependent on the
composition of the steel and the time it spends in the temperature range 370°C to 815°C
(700°F to 1500°F). If a steel has been sensitized, corrosion resistance may be recovered
only by the use of a full anneal (and suitably rapid quench) to dissolve the carbides.
Use of low carbon or stabilized grades are methods of preventing sensitization. The (L
grade) low carbon level limits the amounts of chromium carbides that form, thereby
limiting chromium depletion at the grain boundaries. Sensitization can occur in the
HAZ adjacent to the weldment. Sensitization gives rise to corrosion in the HAZ and is
a prerequisite for polythionic acid stress corrosion cracking.
8 Materials Selection
Guidelines and standards that cover selection and specifications of stainless steels
include international standards, company standards and technical guidelines.
ISO 15156-3 presents materials selection for CRAs for sour chloride containing
environments for upstream applications. Sour corrosion issues are different for refinery
applications and NACE MR103 presents materials selection for CRAs for sour refinery
environments. SABP-A-001 (Polythionic Acid SCC Mitigation - Materials Selection
and Effective Protection of Austenitic Stainless Steels and other Austenitic Alloys)
provides practical advice on mitigation of PASCC in refinery environments. This
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damage mechanism may also affect burner tips and other combustion equipment which
are fired on sour hydrocarbons.
For sour services, UNS S41000 stainless steel (410 stainless steel) and other martensitic
grades must be quenched and double tempered to a maximum allowable hardness level
of 22 HRC. PWHT is also required, since this material is strongly air-hardenable.
Austenitic stainless steel grades offer a combination of good mechanical properties and
material performance at both low (cryogenic) and high temperatures (heat resisting
grades), as well as for a range of corrosive environments. Duplex stainless are
attractive since they offer improved mechanical properties compared to austenitics and
better corrosion resistance in saline environments. Duplex limitations include lower
subzero impact toughness (-50ºC limit) and generally lower tolerance to sour
environments. API TR 938-C (Use of Duplex Stainless Steels in the Oil Refining
Industry-First Edition, 2005) provides advice on duplex steels in refining.
Wrought S17400 stainless steel is permitted for sour service but must be carefully
processed to prevent SSC. ISO 15156-3 specifies two different acceptable heat
treatments for S17400. The maximum hardness level is 33 HRC for both conditions.
Solid austenitic stainless steels are used for cryogenic and other applications, but should
normally be avoided for services above 60ºC, when internal stainless steel cladding is
recommended. Above 60ºC, there is an increased risk of either process-side or external
chloride SCC.
9 Castings
The chemical composition of cast stainless grades is adjusted to increase fluidity and
minimize defects such as porosity and hot tears. Sensitization can occur in the HAZ of
weld repaired areas of higher carbon austenitic grades especially, lowering corrosion
resistance by intergranular attack, which can also promote PASCC.
ASTM A744 requires that castings shall be PWHT (solution anneal and rapid cool)
after all major weld repairs and after those minor weld repairs involving either of the
following conditions: (1) welding on a wetted surface, or (2) welding that heats a wetted
surface to or above 800°F [425°C]. PWHT is omitted from ASTM A743 but is
available as a Supplementary Requirement. ASTM A744 is preferred if non-L grade
steels are specified or allowed. Foundries often make “minor” weld repairs without
PWHT and this practice is generally satisfactory if L (lower carbon) grades are used.
PWHT (solution anneal and rapid cool) should be considered for duplex stainless steel
castings that have been weld repaired. Solution treatment requirements are provided in
ASTM A890.
Document Responsibility: Materials and Corrosion Control Standards Committee SABP-A-022
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10 Fabrication
10.1 Welding and Corrosion Resistance
When stainless steel piping or components are manufactured they are normally
subjected to a final high temperature solution heat treatment (typically at
1050ºC) followed by water quenching. This leaves the material in the solution
annealed condition which is the optimum for corrosion resistance. This heat
treatment gives a poor quality high temperature oxide film on the surface which
is quite thick, porous and cracked. During manufacturing, this oxide film is
normally removed by pickling and passivating the surface in oxidizing acids.
The oxide film which is formed at low temperature, either in the passivating
solution or just by exposure to air, is thin and dense, giving good protection to
the stainless steel. The as-delivered piping is therefore in an optimum condition,
with a solution heat treated microstructure and a well-passivated surface oxide
finish.
When welding is carried out, the metal close to the weld is reheated to high
temperatures, from the melting point at the fusion line to lower temperatures
through the HAZ. An unprotected HAZ which is exposed to air during welding
will therefore show a high level of oxidation. Characteristically, it would be
black in color and in the worst condition may be visibly thick and porous. This
oxide is far more easily broken down than the original passivated surface and
there is a zone of metal under this oxide which is lower in chromium content
relative to the bulk metal.
Therefore, the HAZ has to be protected from re-oxidising at high temperature
during the welding process. This is done by shielding around the weld using an
inert gas to exclude air, thus preventing oxidation whilst the weld metal and
HAZ is hot. Once the weld is cooler, the HAZ will re-oxidise slightly at lower
temperatures but this oxide film is a more protective film than the high
temperature oxide film. This „heat tint‟ oxide formed at the HAZ at lower
temperatures is so thin that it forms interference colors, forming characteristic
blue or rainbow colors. AWS D18.2:1999 addresses factors affecting weld
discoloration inside a 316L austenitic stainless steel tube. It presents a color
guide (Figure 2) relating degree of discoloration to oxygen content in the
backing shielding gas. The heat tint oxide can be identified by a number
corresponding to the oxygen level in the shielding gas. A straw-to-yellow heat
tint (chart no. 3) is considered desirable but a blue tint up to chart no.6 is
acceptable for standard applications.
Heat tint exceeding no. 6 is normally removed by grinding, pickling and
passivating the surface in oxidizing acids. Where welds are accessible,
excessive heat tint can be removed by pickling and passivating the surface using
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standard products. Surfaces should be fully rinsed with clean water to ensure
removal of any residual acids on the surface.
Figure 2 – Weld Discoloration and Heat Tint Numbers
Scanning electron microscopy examination of heavily heat tinted surfaces has
revealed a craze-cracked oxide surface that is enriched in Cr (Figure 3).
Stainless steel lines have failed prematurely in service at heavily heat-tinted
HAZ locations, which was attributed to the heat tint plus poor quality hydrotest
and contributory MIC factors. The craze-cracked surface topography may
promote bacterial colonization.
10.2 Welding of Stainless Steels
Introduction
The purpose of this section is to give information on the correct welding of
stainless steels. It is intended for internal Saudi Aramco operations and
maintenance applications. It also provides guidance for inspection in fabrication
facilities. This section is divided into two parts. The first part gives information
and techniques that are pertinent to the general classifications of stainless steels.
The second part gives consumables and techniques that are specific to individual
grades of stainless steel. This best practice gives general information. If there is
a conflict between this Best Practice and an approved welding procedure then
the approved welding procedure shall govern. All conflicts shall be brought to
the attention of CSD.
10.2.1 Welding Processes
The welding of stainless steels may be carried out using almost any
welding process including all arc welding (Shielded Metal Arc, Gas
Tungsten Arc, Gas Metal Arc, Flux-cored Arc, Submerged Arc and
Plasma Arc), friction, resistance, laser and electron-beam welding
techniques. Stainless steels should not be welded with the oxy-fuel
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welding processes. Within Saudi Aramco we only use two welding
processes: Shielded Metal Arc (SMAW) and Gas Tungsten Arc
(GTAW). Fabricators and contractors may use a wider range of welding
processes depending on their needs. The welding consumables for the
commonly found stainless steels are given in Table 2. The GTAW
process is always used for root passes on butt welds and for butt welds
on pipes smaller than 2" diameter. The GTAW process can also be used
for socket welds. SMAW may be used for the fill passes on butt welds
in pipes larger than 2" diameter and all socket welds.
SMAW Welding
The SMAW welding electrodes for stainless steels are given in AWS
A5.4 specification. Generally, the number of the SMAW welding
electrode is equivalent to the type of stainless steel. For example E316L
electrode is for type 316L stainless steel. SMAW electrodes for stainless
steels come with four usability classifications. These are indicated by
the two numbers following the alloy designation -15, -16. -17 and -26.
For example, E316L-16. The significance of these usability
classifications are as follows:
-15. This is a lime (also called basic) coated electrode. These electrodes
are usable with DCEP (electrode positive) only. Electrode sizes
5⁄32 in. [4.0 mm] and smaller may be used in all positions of
welding. These electrodes tend to weld easier out of position but
are not as smooth. They give superior impact properties at
cryogenic temperatures.
-16. This is a lime - titania (also called basic–rutile) covered electrode.
Electrode sizes 5⁄32 in. [4.0 mm] and smaller may be used in all
positions of welding. This produces a smoother weld bead
appearance than the -15 but is more difficult to weld out-of-
position and a smaller diameter should be selected.
-17. This is a lime - silica - titania covered electrode (also called Acid–
Rutile). This electrode produces a smooth, concave weld bead. It
is generally is not as weldable out-of-position as the -16.
-26. This designation is for those electrodes that are designed for flat
and horizontal fillet welding and that have limited out of position
characteristics. Electrodes with the -26 designation are
recommended for welding only in the flat and horizontal fillet
positions.
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Electrode care, storage and conditioning
Although hydrogen cracking is not a major problem in austenitic steels,
electrodes should not be exposed to humid environments. It may be
possible to recover moist electrodes by baking, however, this is not a
general rule and the electrode supplier should be contacted for advice on
a case by case basis. It is very important to keep electrodes for
dissimilar metal welds in a low hydrogen condition. Failure to do this
can result in hydrogen cracking on the non-austenitic side of the joint.
Dissimilar metal welds are not permitted in sour service exposure.
Dissimilar metal welds in hydrocarbon service must be made with a
nickel based consumable.
SAW Welding
The high heat input from SAW leads to larger weld beads and slow
cooling rates. This may lead to problems with hot cracking. Hot
cracking is caused by the segregation of minor elements to the liquid
phase during freezing. One of the elements that can cause this
phenomenon is silicon and, due to the slow cooling rates from SAW,
silicon pickup from the slag can be quite significant. Ferrite control in
submerged arc welds is therefore very important, but this may be
problematic due to the difficulty of control over dilution in the weld.
Base metal dilution during SAW can vary between 10 and 75%, more
than any other arc welding process. Careful control must be maintained
over the arc during welding as small variations in penetration can greatly
affect the dilution levels. Electrode wire is readily available from a
number of different suppliers. Flux for SAW is usually designed to be
either basic or neutral with respect to the steel; however, no AWS
specification exists to cover these fluxes. Neutral fluxes give sound weld
deposits and permit some oxidation and loss of alloy to the flux. Basic
fluxes contain additions of alloying elements that are imparted to the
weld when molten. Fluxes can be susceptible to pickup of moisture and
should be baked as per the manufacturer's instructions prior to use.
Moisture in the flux can lead to defects such as wormholes and porosity.
GTAW Welding
GTAW (Gas Tungsten Arc Welding also referred to as TIG) is similar to
Gas Metal Arc Welding (GMAW) in that the arc is protected by an inert
gas. An arc is established between a tungsten electrode and the work
piece. The filler material is added separately into the molten weld
puddle. Since the filler material does not form part of the arc, there will
be extremely low loss of alloying elements during welding. All grades
of weldable stainless steel may be welded using GTAW welding, giving
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a high quality weld. GTA welding has extremely wide applicability and
can be used to weld in all positions. It may be used to weld any
thickness of material; but is most suited to thin sections. Only inert gases
are used during GTA welding. Argon is primarily used for both
shielding the arc and back-purging. Helium shielding provides deeper
penetration, which is useful for thicker sections. Contact between the
electrode and the weld pool is to be avoided to avoid tungsten
contamination. Back-purging to protect the root of the weld is important
when GTA welding stainless steels to control oxidation of the weld area.
Argon is typically used for this purpose.
FCAW Welding
Electrodes for FCAW are designated according to AWS specification
A5.22. This designation takes the form EXXXTY-Z wherein XXX
denotes the chemical specification of the steel (e.g., 308), Y denotes the
applicable positions for welding (1 for all position and 0 for flat or
horizontal only) and Z the shielding gas (1 for CO2; 3 for self-shielding,
(i.e., no gas); 4 for 75 - 80% Ar in CO2 , and G for unspecified). It is not
unusual for bismuth to be added to the flux of flux cored arc welds; this
facilitates ease of flux removal after welding. However, bismuth
additions should not be employed for components which will operate at
high temperatures or require a postweld heat treatment. This is due to
the link between bismuth and reheat cracking susceptibility. Saudi
Aramco does not approve the use of self-shielded (No shielding gas)
FCAW welding for stainless steel.
Electroslag Welding
Electroslag is frequently used for overlay welding in fabrication shops.
It has very low dilution and can be used for single or multi-pass overlays.
Austenitic Stainless Steel Properties Affecting Welding
The coefficient of thermal expansion for the austenitic stainless steels is
almost 40% greater than that of carbon steel. This means that distortion
is generally more of a problem with austenitic stainless steels and must
be considered during welding.
The thermal and electrical conductivity of austenitic stainless steel is
lower than that of carbon steel. Less welding heat is required to make a
weld because the heat is not conducted away from a joint as rapidly as in
carbon steel. This also makes the weld puddle more fluid and difficult to
control.
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Purging and Shielding Gas
A chromium oxide layer forms when stainless steel is exposed to air and
normally acts as a thin passive layer. This layer becomes thicker at
higher temperatures. This chromium oxide can adversely affect the
corrosion resistance of the weld and heat affected zone. The chromium
oxide has a very high melting point (2435°C). This is much higher than
the stainless steel base or weld material which is nominally 1450°C. It
will interfere with the fusion of the welding process and cause an
unacceptable weld profile. For these reasons the weld and Heat Affected
Zone (HAZ) must be protected from the air by an inert gas. This gas
protection is known as a shielding gas and a purge gas.
Areas that have been exposed to high temperatures but did not have, or
had insufficient, gas shielding will form a 'heat tint‟. This heat-tinted
area will have comparatively poor corrosion resistance when compared
with standard plate due to the heat tint oxide giving little protection to
the base metal underneath, along with the base material being depleted of
chromium immediately under the tint. The corrosion resistance of the
component can only be restored by removing the oxide and chromium
depleted layer. A three-step process of grinding, pickling and rinsing is
best. (section 10.5) Pickling pastes or baths should be used at such
strength and duration so as to remove fully the oxide and chromium
depleted layer, but not stain or unduly corrode the surface. Rinsing
solutions should, preferably, be de-mineralized water.
Argon is normally used as the shielding gas on the torch for the GTA
welding process. Argon/Helium and helium gas can also be used but are
not common.
The SMA welding process does not require a shielding gas because it
generates its own protective shielding from the flux during welding.
For groove welds in pipe the back side of the weld must be protected by
a purging gas. Argon is normally used as the purging gas.
Safety Caution
Argon is heavier than air. Though it is not toxic it can cause death by
asphyxiation. Always be aware of this when purging in tanks, vessels or
other areas where argon can accumulate. Never enter a pipe if it has a
purge running.
For the purge to be effective it must reduce the oxygen content on the
back-side of the weld to less than 0.05% (500 ppm). Purge dams must
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be installed to contain the purge gas. See the sketch below. There are
many types of purging dams (i.e., cardboard, plastic, wood, balloons, and
water soluble paper.) There are commercially available purging devices
which are recommended because they seal well and reduce the purging
volume. It is critical that the purge dam is tight and can retain the
purging gas. It will not be possible to achieve a good purge if the purge
dam is porous or leaks. The purging volume should be kept as small as
possible.
Figure 3 – General Purge Dam Configuration
Water soluble paper is porous and several layers of it must be glued
together to make it gas tight. Water soluble paper must be installed with
water soluble tape and water soluble glue. Water soluble dams should be
the last choice for purging dam material.
If a purge oxygen monitor is not available then the following table can
be used as a guideline for minimum purging time. This table is only
applicable if there is no leakage of gas through the purge dam. If this
table is used, then the inside of the first portion of root welded must be
examined through the root gap to make sure that there is no excessive
oxidation.
The flow rate shown for this table is 50 CFH (22.5 L/H). Once the purge
has been established the flow rate should be reduced to 10CFH or just
enough to maintain the purge level. If there is excessive purge flow it
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can buildup pressure on the inside of the pipe and cause the root to be
defective or unweldable.
Purge Times for Stainless Steel Pipe
Diameter Purging time
Minute
2 and less 0.5
4 1
6 2
8 3
10 4
12 6
16 10
18 12
24 22
Minimum purging time based on pipe size and 6 volume changes of gas
The above table assumes use of argon gas at a flow rate of 50 CFH
(22.5 L/H). Listed times are for each 300 mm of pipe length to be
purged (multiply by actual length). Use the above values for 300 mm for
any shorter length.
Preheat, Interpass Temperature, Heat Input and Post Weld Heat Treatment (PWHT)
The following section provides general information on the preheat,
interpass temperature, heat input and PWHT for stainless steel materials.
The governing code, Saudi Aramco Standards and approved welding
procedure must be followed.
Austenitic, Super-Austenitic, Duplex and Precipitation Hardening Stainless
Austenitic, super-austenitic, duplex and precipitation hardening stainless
steels are susceptible to sensitization and secondary phase embrittlement
when exposed to temperatures in the range of 450°C to 850°C. For this
reason preheat is not used for these materials. They can be heated to
remove moisture prior to welding if required.
To limit sensitization and embrittlement, the maximum interpass
temperature is restricted for these materials. For types 304L and 316L
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the interpass temperature shall not exceed 177°C. For all other stainless
steels in this group the interpass temperature shall not exceed 100°C.
The heat input for these materials must also be kept as low as possible.
For the duplex materials there is a heat input range that is maintained in
order to obtain the “duplex” microstructure in the weld. This range will
be indicated on the welding procedure. GTA Welding without the
addition of filler material is expressly prohibited for this material. This
can reduce the corrosion resistance and lead to cracking. Sometimes
welders will want to weld without filler consumable to smooth a rough
weld profile. This should never be done. Filler material must always be
added or the area should be ground.
Post weld heat treatment (PWHT) is not normally recommended for
these materials because it can cause sensitization. However, the “L”
grades and types 321 and 347 will not be sensitized by a normal PWHT.
If heat treatment must be performed it is often specified as a Solution
Anneal heat treatment. This treatment involves heating the material to a
temperature of approximately 1000°C to 1200°C. This relieves the
stresses from forming and welding and is above the temperature at which
sensitization occurs. The material is then quickly cooled through the
sensitization range.
1. Ferritic Stainless Steels
Preheat must be used for the ferritic stainless steels. This is because
these materials can be hardened due to the fast cooling from the
welding temperature. 250°C preheat should be used. The Interpass
temperature is restricted to 315°C. The heat input is not a serious
concern for these materials. PWHT is not normally required for
these materials unless the thickness exceeds 38 mm.
2. Martensitic Stainless Steels
These materials will readily form martensite when air cooled. The
preheat temperature range is from 250°C to 450°C. After welding
they should be slow cooled to 120°C (martensitic transformation
temperature) and then tempered at 750°C. The Interpass temperature
is restricted to 315°C. The heat input is not a serious concern for
these materials.
Contamination
As discussed further in section 10.4, it is important to avoid
contamination of the stainless steel with particles of carbon steel or
elements which can adversely affect the corrosion resistance or cause
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cracking. Stainless steel wire brushes must always be used. All grinding
discs must be halogen, sulfur and iron free as indicated by a statement
“for stainless steel.” Brushes and grinding wheels used on stainless
steels should either be new or only previously used on similar stainless
steels. Brushes and grinding disks that have been used on carbon steel
must never be used on stainless steel. Stainless steel must be fabricated
in a separate shop from carbon steel. One of the greatest sources of
carbon steel contamination is through grinding dust from the carbon
steel. This can be embedded into the stainless steel by walking on the
stainless steel with contaminated shoes, contaminated lifting equipment
and contaminated tools.
Other contamination can be from grease, paint and dirt. These can cause
significant pickup of carbon and other elements which may affect the
corrosion resistance. Before any welding operation, it is essential to
ensure that all of the components are clean. If a multipass weld is being
produced, all slag and surface oxide must be removed between passes.
Copper, zinc, tin, lead and other metals may be picked up from
fabrication tools and can lead to cracking. These elements are strongly
linked to hot cracking due to the formation of low melting point alloys.
Ferrite In Weld Deposits
One of the problems associated with welding of austenitic stainless steels
is that of solidification cracking. This problem is often referred to as 'hot
cracking' since it occurs before the weldment has cooled. The presence
of ferrite in the weld reduces the susceptibility of the metal to hot
cracking. This ferrite is referred to as “Delta ferrite” and can be
observed in the as-deposited microstructure of austenitic stainless steels
welds. This is a product of the solidification and transformation
sequence experienced at elevated temperature. For certain alloys it is not
essential to have ferrite in the weld deposit but normally 3 – 7FN ferrite
will prevent cracking. Cracking is more of a problem when the welds
are restrained or the joints are large. Ferrite increases the weld strength
level. Ferrite may have a detrimental effect on corrosion resistance in
some environments. It also is generally regarded as detrimental to
toughness in cryogenic service. In high-temperature service delta ferrite
can transform into the brittle sigma phase. Materials with a ferrite
number greater than 10 will be susceptible to the formation of excessive
quantities of sigma phase and should not be used for elevated
temperature service (i.e., at temperatures exceeding 650°C).
Ferrite can be measured on a relative scale by means of various magnetic
instruments. Ferrite percentage can also be determined by
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metallographic examination. The amount of ferrite in austenitic stainless
steel welds can also be predicted from the chemical composition of the
weld deposit using one of several constitution diagrams. These diagrams
use nickel and chrome equivalence empirical relationships. These
diagrams are known as the Schaeffler, DeLong, and the Welding
Research Council (WRC). The WRC diagram should be used for ferrite
predictions and gives a ferrite number. Ferrite can be expressed as a
“percent ferrite” or a ferrite number (FN). The relationship between the
percent ferrite and ferrite number is complex. It is based on the cooling
rate and alloy interaction. TWI has weld simulation software online that
can predict the percentage ferrite
http://www.twi.co.uk/j32k/protected/toolkits/Ferrite/IntroInstructions.html.
Two rule-of-thumb conversions from FN to percentage are:
1. For low percentages of ferrite (less than 10) the FN is the same as
the percentage.
2. For higher percentages (duplex)
0.70(FN) = % ferrite
Measurement of ferrite content in DSS, however, is currently performed
with a magnetic measuring technique and is more commonly referred to
in terms of percentage.
SAES-W-016 gives ferrite measuring requirements for welding
procedure qualification and production and special requirements for
duplex materials. SAES-W-014 gives ferrite requirements for overlays.
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Figure 4 – WRC Ferrite Number
Weld Overlay Cladding
Weld overlay cladding is the process of depositing a layer (or layers) of
austenitic stainless steel (or other corrosion or wear resistant material)
onto the surface of a base material (such as mild steel). This layered
component can provide corrosion resistance and/or wear resistance
without the expense of producing it entirely from a higher alloy material.
Submerged arc welding is by far the most common method of cladding
with austenitic stainless steel. SAW is ideally suited to the task since
relatively large areas may be deposited with high deposition rates.
Electroslag welding is often frequently used. Less frequently are GTAW
and GMAW and FCAW welding processes. There is a variety of
different equipment available, employing either strip or between one and
six wires. Dilution of the weld pool with molten base material may be a
problem during cladding since the underlying materials may contain
elements detrimental to the performance of the stainless steel (e.g.,
carbon). In these instances, dilution could be minimized but this may be
difficult since it is very sensitive to arc length and voltage.
Alternatively, multiple layers can be deposited so that dilution with the
parent metal is reduced in each progressive pass. Multiple layer overlays
are preferred and single layer overlays require special approval.
Joining of Clad Materials
There are two techniques for joining of carbon steel which is clad with
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stainless steel: Single-sided and double-sided:
1. Single-sided
When welding clad materials from one side (for example a small
diameter pipe joint) the entire weld will be made with a
consumable that is compatible with the dissimilar metal welding of
the base material and the CRA.
Figure 5 – Single-sided Cladding
2. Double-sided
The entire weld is made from both sides (See Saudi Aramco
Drawing AB-036367). The stainless steel must be “stripped back”
by grinding or machining to no closer than 10mm from the edge of
the carbon steel weld. The “stripped back” area shall be checked
with a copper sulfate solution to verify that all of the stainless steel
has been removed.
Copper sulfate solution preparation:
4 gm copper sulfate pentahydrate CuSO4.5H20 (use reagent grade).
250 ml of distilled water.
1 ml sulfuric acid H2SO4 (specific gravity 1.84).
The solution is swabbed on the part, and left to stand for 6 minutes
minimum, the part should be carefully rinsed and dried. If copper
deposit is observed, then free iron is on the surface of part.
(Reference ASTM A967)
The carbon steel shall be completely welded and NDE inspected
prior to welding the cladding portion.
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Figure 6 – Double-sided Cladding
Caution: Never weld carbon steel or low-alloy steel into high alloy, stainless steel or nickel base material. Never weld stainless steel electrode into nickel base material.
Welding of Duplex and Superduplex
Duplex stainless steels (DSS) are broadly divided into standard and
superduplex stainless steels. These materials are characterized by high
strength, good corrosion resistance, good resistance to chloride stress
corrosion cracking and relatively good notch toughness. Duplex
stainless steels (DSS) contain 35 to 65% ferrite and the remainder is
austenite. The percentage of ferrite is also called the phase balance.
Duplex stainless steels that are currently produced tend to have slightly
more austenite that ferrite. The table below gives an approximate
comparison between the chemistry of the Duplex and the Superduplex.
Figure 7 – Duplex Microstructure, magnification approximately 200X
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Table 3 – Typical Chemistry of Duplex
and Superduplex Stainless Steels
Cr (%) Ni (%) N (%) Mo (%) Fe
Standard Duplex Chemistry
22 5 0.12 3.2 Balance
Superduplex Chemistry 25 7 0.25 3.5 Balance
Besides the phase balance, there is a second major concern with duplex
stainless steels. Intermetallic phases (Sigma and chi) form at the
temperature range of 540 to 950°C. These phases can significantly
reduce the toughness and corrosion resistance of these materials. These
phases can be eliminated and the original properties restored if the
material receives a solution anneal heat treatment at 1040°C and is
rapidly cooled through the critical temperature range. The addition of
nitrogen significantly delays formation of these phases. Therefore, it is
critical that sufficient nitrogen be present in these alloys.
The characteristics of welding duplex stainless steel are very similar to
welding 300 series stainless steels. The same welding processes, joint
details and techniques are generally followed. Some of the differences
are noted below.
There is an increased emphasis on heat input control. Both the upper and
lower ends of the heat input range must be established on the welding
procedures in order to achieve the proper phase balance. Welding at
lower heat inputs promotes higher ferrite levels; whereas welding at
higher heat input levels promotes lower ferrite levels. The heat input is
based on the following formula. Generally, the range on heat input for
duplex stainless steel is 0.5 to 2.5 KJ/mm but the heat input restrictions
on the welding procedure must be followed.
dTravelSpee
voltsampsHeatInput
60**
Preheating is not recommended with duplex stainless steels except to dry
the surface or when the temperature is below 5°C [40°F], or when
welding heavy sections under restraint.
The maximum interpass temperature for duplex stainless steels is 100°C
per the Saudi Aramco specification SAES-W-016. The low interpass
temperature reduces the amount of sigma formation in the HAZ.
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Autogenous welding (welding without filler material) should not be
performed on duplex stainless steels.
DSS welds tend to be higher in ferrite than the base metal being welded.
There are near matching composition proprietary filler metals for many
of the standard and super DSSs. Suggested filler metals are shown in
Table 2. It is also advisable to consult the alloy producer of proprietary
alloys for their filler metal recommendations and filler metal availability.
Nickel alloy filler metals have also been used to weld both the standard
and super DSSs. One such nickel alloy filler metal for which data is
available is AWS A5.14 ERNiCrMo-3. Since the nickel alloy welds are
fully austenitic, there is no concern regarding obtaining a balance of
austenite and ferrite. This material meets the strength, corrosion
resistance and impact resistance of the base materials.
Dissimilar metal welds between DSS and austenitic stainless steels such
as Type 304 or 316 or for welding to carbon steel should be made with
ENiCrMo-3 or ERNiCrMo-3.
Because of the ferrite present in the duplex stainless steels there is a
possibility of delayed hydrogen cracking. For this reason all welding
electrodes must be handled to insure that they are low hydrogen. All
surfaces to be welded must be free from contaminants that could cause
hydrogen pickup.
Dissimilar Metal Joints
Dissimilar metal weld joints are welds between stainless steel and
another type of alloy. This is frequently stainless steel welded to carbon
steel or a low alloy steel. Consideration must be given to the possibility
of galvanic corrosion in this type of joint. It is very important to keep
electrodes for dissimilar metal welds in a low hydrogen condition.
Failure to do this can result in hydrogen cracking on the non-austenitic
side of the joint. Dissimilar metal welds are not permitted in sour service
exposure. Dissimilar metal welds in hydrocarbon service must be made
with a nickel base consumable, such as E/ERNiCrMo-3. Austenitic
stainless steel (i.e., type 309) may only be used for dissimilar metal
welds in non-hydrocarbon, non-sour service (i.e. water, air or steam) or
external attachments.
Sensitization
Sensitization occurs in the HAZ adjacent to the weldment and may be
minimized by using either low carbon or stabilized grades of stainless
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steel. If a steel has been sensitized, corrosion resistance may be
recovered only by the use of a full anneal (and suitably rapid quench) to
dissolve the carbides. Some degree of corrosion resistance may be
recovered by a stabilization anneal, typically in the region of 900°C.
Sensitization gives rise to corrosion in the HAZ and is a prerequisite for
polythionic acid stress corrosion cracking. Low carbon grades or grades
with Ti or Nb stabilization can prevent or reduce sensitization.
Embrittling Phases
Another phenomenon similar to sensitization is the precipitation of Chi
and Sigma intermetallic phases on the grain boundaries in the HAZ.
The precipitation of any secondary, chromium-rich phase will deplete the
local area of chromium.
The classic sigma-phase is nominally FeCr composition, but it can have
a more complex, variable composition. High molybdenum high strength
stainless steels can contain the Chi phase (Fe36Cr12Mo10). The presence
of this phase, which normally occurs at grain boundaries, depletes the
chromium content leading to intergranular corrosion. This may cause
alloy embrittlement during long term use. The presence of such phase
has proven to be highly sensitive to alloy processing parameters such as
the cooling rate after a final heat treatment. Both and phases can be
easily formed by the decomposition of ferrite, at 540-950°C for
phase and 650-950°C for phase. If these precipitates form a
continuous network there can be a corresponding reduction in ductility,
toughness and corrosion resistance. Recent alloy developments have
included the addition of significant amounts of nitrogen to high alloy
stainless steels, this acts to retard the nucleation of both and phases,
meaning that thick plate can be successfully multi-pass welded.
Microsegregation
Pitting of the weldment, independent of any precipitation, may occur
where micro-segregation and coring within dendrites is particularly
severe. This can often be the case if a matching filler, autogenous weld
or high molybdenum stainless steel (4-6% Mo) is used or if there are
large surface-lying dendrites. This is the reason that high molybdenum
grades must be welded with nickel base fillers.
Crevice Corrosion
Crevice corrosion is another frequent cause of failure in weldments.
Possibly the most frequent cause of crevice corrosion are solidification
cracks and microfissures. Smaller microfissures are often invisible to the
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naked eye and therefore microfissure crevice corrosion is often mistaken
for simple weldment pitting. As previously stated, solidification cracks
may be avoided by proper control of weldment delta ferrite content. Any
welding defect that causes a crevice or confined feature can also lead to
crevice corrosion. Such defects include flux layers or inclusions, pores,
and weld start/stop cracks and craters. Moreover, poorly adherent weld
spatter may also create crevices. Bad joint design and/or poor welding
practice can also cause crevice corrosion; for example, non-removable
backing rings are to be avoided or, if essential, should be fully consumed
during welding. Failure to do this may result in crevices being formed
between the component and the backing ring. Microfissuring and
crevice corrosion in high molybdenum alloys (4-6%) is best avoided by
the use of nickel base fillers.
10.2.2 Fume and Welding Safety
Normal safety considerations should be taken when welding austenitic
stainless steels. Austenitic stainless steels also generally contain nickel
and this may lead to sensitization of the skin. Sensitization may be as
minor as mild irritation, or as major as gross swelling. Particular care
should be taken to minimize exposure to weld fumes. Fumes from the
welding of stainless steels may also contain significant quantities of
nickel and hexavalent and trivalent chromium. Chromium is toxic by
inhalation; therefore, welding should only be carried out using proper
fume extraction. Chromium and nickel are both known carcinogens and
typically have maximum exposure limits as specified in the MSSG. It
should be noted that MIG and TIG welding can also give rise to ozone;
this also necessitates suitable ventilation.
Table 2 – SMAW And GTAW Consumable Selection, Preheat and PWHT
Austenitic Stainless Steels
Parent Material Type
Filler Material
SMAW Electrode
GTAW Bare Wire
Preheat PWHT Comments
304 and 304L E304L ER304L 20° and dry none
304H E304H ER304H 20° and dry none
316 and 316L E316L ER316L 20° and dry none
317L E317L ER317L 20° and dry none
310 E310 ER310L 20° and dry none
321 E347 ER347 20° and dry none
330 E330 ER330 20° and dry none ENiCrFe-3 and ERNiCr-3 can also be used
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Austenitic Stainless Steels
Parent Material Type
Filler Material
SMAW Electrode
GTAW Bare Wire
Preheat PWHT Comments
347 E347 ER347 20° and dry none ENiCrFe-3 and ERNiCr-3 can also be used
Martensitic Stainless Steels
Parent Material Type
Filler Material
SMAW Electrode
MIG, TIG, SAW
Bare Wire Preheat PWHT Comments
410 E410 ER410 250°C required
430 E430 ER430 250°C required
Ferritic Stainless Steels
Parent Material Type
Filler Material
SMAW Electrode
GTAW Bare Wire
Preheat PWHT Comments
405 E309 ER309 250°C Not normally
required
410S E309 ER309 250°C Not normally
required
Superaustenitic, Precipitation Hardening
Parent Material Type
Filler Material
SMAW Electrode
GTAW Bare Wire
Preheat PWHT Comments
904L E385 ER385 20° and dry none E/ER NiCrMo-3 may be used
254SMO ENiCrMo-3 ERNiCrMo-3 20° and dry none
Alloy 20 ENiCrMo-3 ERNiCrMo-3 20° and dry none
17-4 PH ENiCrMo-3 ERNiCrMo-3 20° and dry none
Duplex and Super Duplex
Parent Material Type
Filler Material
SMAW Electrode
GTAW Bare Wire
Preheat PWHT Comments
S31803 S32205 J92205
E2209 ER2209 20° and dry none
S32550 S32750 S32760
CD-4MCu (cast)
E2595 ER2594 20° and dry none E/ERNiCrMo-3 may be used
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10.3 Storage
Storage areas must be clean, dry and well ventilated. Absorbent wrappings such
as interleaving paper, cardboard and timber should be kept dry to prevent
surface staining. Plates and sheets should be stored vertically in racks and not
be dragged out of the racks or over one another. Racks should be protected to
prevent iron contamination. Outdoor storage of stainless steels adjacent to
carbon steels should be avoided (Figure 9).
Figure 8 – Microcracked Surface at Heat Tint
Oxide Films on 316L Stainless Steel, x200.
Figure 9 – Unsuitable Materials
Separation and Outdoor Storage
10.4 Shop Fabrication
The number one problem with unsuccessful fabrication of stainless steel is
surface contamination. The shop should have a separate area where only
stainless steel is fabricated. This will prevent the cross-contamination of the
stainless steel surface with iron particles.
NiDI publication 11003 highlights that: “experience has shown that (surface)
cleanliness and weld quality are far more critical to successful performance than
Cl-ion concentration”. Some suggested methods for the removal of surface
contamination and defects are presented in Table 1. NZSSDA (Code of Practice
for the Fabrication of Stainless Steel Plant & Equipment, 2001) stresses that the
fabricator must ensure that the fabrication is clearly identified and protected
from damage and contamination. “Mild steel lifting forks, hooks, chains and
wire ropes shall be kept from coming into contact with stainless steel
equipment”. Plastic-coated or SS weld overlayed parts should be used for
handling SS. Cleaners which can be used include stainless steel wool and
stainless steel wire brushes, provided that they have not previously been used on
non-stainless steels.
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Figure 10 shows an unacceptable example of poor material segregation, where
carbon and stainless steels are being processed together. Figure 11 shows an
example rust spotting caused by iron contamination.
Figure 10 – Poor Shop Material Segregation
Figure 11 – Iron Contamination Caused by
Operator Grinding Carbon Steel Nearby
10.5 Pickling, Passivation and Iron Removal
Chemical passivation is normally only used to remove “free iron”, high
temperature oxides and other surface contamination arising from processing and
handling. Pickling treatments provided in ASTM A380 include the following:
Typical austenitic stainless steel pickle solution: 10% HNO3 + 2% HF at
50ºC
Removes oxide film plus 25 – 40 μm of surface
Effectively removes welding heat tint
Removes embedded iron particles
Can improve corrosion resistance of ground, wire brushed and blasted
surfaces by removing surface contamination and exposed impurities in the
metal, such as sulphides
Exposes a new, clean surface which can then be passivated
Air passivate or be chemically passivated
Pickling is normally performed during manufacturing processes, such as
following solution heat treatment of welded stainless pipe. The parts are picked
by immersion in a bath and thoroughly rinsed and blown air dried afterwards.
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Pickling can also be performed after shop or site welding operations, using
proprietary pickle pastes or swabbing followed by thorough rinsing in clean
water. Chemical passivation, using nitric acid treatments, etc., is also normally
used during manufacturing after pickling treatments.
Pickling with nitric-hydrofluoric acid removes free iron and a thin surface layer
of metal that may contain surface defects. The metal surface is then passive and
in the most corrosion resistant state. If a nitric-hydrofluoric acid pickle is not
practical, the free iron can be removed mechanically. Acceptable methods
include the use of medium to fine-grit abrasives such as clean flapper wheels,
flexible disks or blasting with clean abrasives such as glass beads, garnet or
walnut shells. Free iron and heat tint can also be removed by a hand-held
electropolishing probe.
The “Rust Bloom” water wetting and drying procedure described in ASTM
A380 para 7.2.5.1 is an effective test to check for the removal of free iron. The
procedure calls for wetting the surface with distilled or deionized water or fresh
water followed by drying. Formation of rust stains may be accelerated by
periodically wetting the surface with preferably distilled or deionized water or
clean, fresh, potable tap water. The wet-dry cycles should be such that the
sample remains dry for a total of 8 h in a 24-h test period. After completion of
this test, the surface should show no evidence of rust stains or other corrosion
products.
Free Iron Contamination is detected using a ferroxyl test. A solution of nitric
acid and potassium ferricyanide is sprayed onto the surface and free iron
contamination is disclosed by the development of a dark blue color within 30 s.
The solution should be removed after a few minutes with a damp cloth or water
spray. ASTM A967 Practice E (Potassium Ferricyanide–Nitric Acid Test)
provides further details of this type of test, which is recommended for
application only on 200 and 300 series stainless steels.
SAES-W-014 recommends that only stainless steel brushes, ceramic (glass)
beads, iron-free grit, or stainless steel grit shall be used to mechanically clean
the weld overlay surfaces.
10.6 Field Fabrication
Shop fabrication is normally better controlled and potentially much more serious
field fabrication errors could be overlooked. Some contractors apparently lack
knowledge and/or experience of appropriate handling techniques for stainless
and other CRAs.
Storage racks, forklift truck forks and handling tools, etc., must be coated with
suitable materials such as plastic, rubber or weld overlayed with SS. Alternative
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lifting equipment materials to those used in carbon steel fabrications shops are
also recommended. Fabric or rope slings should be used rather than steel
chains. Conveyor tables should be designed and operated to avoid damage and
contamination. Where hardened ferrous tools (such as roll, presses and angle
rolls) must be used, they must be completely cleaned (solvent/steam cleaned).
Heavy paper sheets are sometimes used to prevent direct contact between tool
and stainless steel.
Packaging materials and methods used must help prevent surface damage.
Carbon steel strapping must not be allowed to come into contact with the
stainless steel surfaces. If used, wooden bearers should be inserted between the
carbon steel strapping and the stainless steel surfaces.
Table 4 – Suggested Removal Methods for Various Surface Defects and Contamination
The following photographs (Figures 12 to 15) show improper handling of SS
and are from an actual jobsite. Contractors seemed totally unaware of
appropriate techniques for good fabrication practice for stainless steels.
Examples included: contractors off loading stainless steel pipe with carbon steel
hooks, using carbon steel wedges to support stainless steel during tank
fabrication, using wire brushes and grinding wheels that were first used on
carbon steel, using carbon steel lifting brackets to place shell plates, not
covering the storage facilities so the stainless steel does not rest on carbon steel
and other items.
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11 Hydrostatic Testing
SAES-A-007 paragraph 6 limits the chloride content of hydrotest water to 50 ppm to
minimize the risk of chloride pitting or SCC during startup. Hydrotest water should
also be verified as low chloride and low SRB bacteria count, or be biocide treated. For
example, use Kitagawa or Draeger tubes or similar field techniques, to verify chloride
level on-site (Figure 16).
The key actions are summarized:
Hydrotesting should be carried out with clean treated water
Do not use untreated raw water, seawater, or contaminated recycled water
Drain water from inside plant promptly after hydrotesting
After draining hydrotest water, check that there are no areas of ponding (stagnant
water) – if necessary, wipe / mop to dry
Figure 12 – Carbon Steel Wedges
on Stainless Steel Tank Bottom
Figure 13 – Carbon Steel Fitting Plates
Used to Fit Stainless Steel Shell Plates
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Figure 14 – Carbon Steel “Key Nut”
on Stainless Tank
Figure 15 – Carbon steel Fixturing
(Wedges and Key Shims) on Stainless Tank
Figure 16 – Kitagawa Chloride Test Tube # 201SB
12 Microbiologically Influenced Corrosion (MIC)
MIC is a fairly common problem with stainless steels, including duplex stainless grades.
Failures can occur rapidly in microbially contaminated waters containing relatively low
chlorides (<100 ppm). These failures can occur too rapidly (in terms of weeks to
months) to be attributed to conventional chloride crevice corrosion. The morphology of
MIC failed components is usually consistent with localized corrosion and pitting at or
adjacent to austenitic stainless welds (Figures 17, 18). According to the ASSDA, MIC
can be avoided as follows:
Ideally, ensure all internal welds are polished smooth – bacteria can form colonies
on rough weld surfaces. Though this may be impractical in many engineering
applications, weld spatter should definitely be removed or controlled (Table 4).
Remove heat tints, as these favor bacterial colonization
Use only treated water for hydrotesting and for cooling water: microorganisms
cannot live in treated (chlorinated) water
Introduce a biocide such as chlorine into the water system
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Do not leave stainless equipment, such as tanks, pipes and vessels, filled with
stagnant water
Note frequently there is confusion between the “chloride” that causes stress corrosion
cracking and the “chlorine” found in the biocides used to treat water. “Chloride” is the
ion of Chlorine (Cl-) that is present in water from dissolving NaCl, MgCl2, or other
salts. The “chlorine” that is present in water from some of the biocides is HOCl and
OCl-. These forms of “chlorine” are sometimes referred to as “free chlorine.” They do
not break down or change into the harmful “chloride” ion that causes stress corrosion
cracking.
Figure 17 – Stainless steel water tank after
8 months, showing preferential corrosion
of welds by MIC, where heat tints were not
removed.
Figure 18 – Microsection through a SS tank
weld showing undercut pitting due to MIC
in weld filler metal. 316L plate and filler
metal were damaged in 6 weeks due to MIC
in raw water
Remedial measures include: drain promptly and completely after hydrostatic testing, or
circulate water for about one hour daily if the water cannot be drained. Regarding
draining and drying, valves, for example, should not be overlooked and must be drained
fully.
13 Coating Stainless Steel
13.1 Coating Under Insulation
To mitigate CUI, stainless steels operating at low and high temperatures ranges
are insulated and normally the SS is coated. For SSs, CUI damage can
potentially occur as SCC, pitting and crevice corrosion. Insulation is normally
encased in aluminum sheet wrapping. Causes of CUI-related failures can
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include moisture entrapment under insulation, chloride contamination of
insulation and damaged or non-weatherproof casings.
NACE RP0198 (The Control of Corrosion Under Thermal Insulation and
Fireproofing Materials - A Systems Approach) provides practical guidelines for
managing CUI. It is also very important to specify and install low leachable
chloride insulation materials for SSs (conforming to ASTM C871). External
coating selection shall be reviewed and approved by the CSD Coatings Team.
13.2 Coating above Grade Piping Exposed to Atmospheric Conditions
Exposure to chloride contamination due to washing down with saline or raw
water and proximity to seawater breeze or splash can cause significant damage
to plant piping and equipment made of stainless steel. To prevent chloride
induced stress corrosion cracking caused, protective coating shall be used.
Select halide free coating materials which need minimum surface preparation
either by solvent cleaning or by abrasive blasting using aluminum oxide
abrasive without causing damage to the passivation layer.
13.3 Coating Buried Pipes
All buried stainless steel pipes shall be coated to prevent adverse interference
with the cathodic protection system. In addition, stainless steel pipes are
susceptible chloride stress corrosion cracking due to exposure to soil chloride
contamination and soil stress, and hence, halide free external coating shall be
applied on stainless steel pipes after appropriate surface preparation with solvent
cleaning and/or abrasive blasting using aluminum oxide abrasive.
14 Summary
The flowchart (Figure 19) summarizes five principal process steps for the specification,
fabrication, hyrotesting and protection of stainless steels.
The controls associated with each step should be carefully followed and documented
where required, to ensure an optimum performance and reliable installation using
stainless steels. The controls should be used as a checklist to document the use of
correct materials and proper storage, fabrication, hydrotesting and insulation and
external coating (where appropriate).
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Process Step Control
Figure 19 – Flowchart summarizing principal process steps and associated controls in the
specification, fabrication, hydrotesting and protection of stainless steels Revision Summary
25 August 2008 New Saudi Aramco Best Practice.
Storage and
Segregation
Stainless Steel
Selection and
Specification
Consider service, PREN
Review heat treatment of
wrought and cast parts
Perform PMI
Store SSs separately in dry conditions
Avoid free iron contamination
Use non-chlorinated solvents and
chloride-free marking inks
Fabrication and
Assembly –
Shop and Field
Hydrotest
Procedure and
Documentation
Protection
Insulation and
External Coating
Verify hydrotest water chloride (≤ 50 ppm)
and low SRBs (SAES-A-007)
Completely drain and dry water after test
Don’t leave trapped stagnant water
Verify low leachable chloride
insulation
External coating holiday check
Water tightness of sheathing
Control or remove welding heat tints
Check for and remove any iron contamination
Check appropriate handling, tools and equipment
Welding procedure control – PMI of consumables
& fabricated parts