Steam Valves

Inspect steam valves for stellite delamination

By Kim Bezzant, Structural Integrity Associates Inc

Stellite liberation from large valves installed in high-pressure (HP) and hot reheat (HRH) steam systems serving F-class combined cycles has emerged as an important industry concern. Tight shutoff of parallel-slide gate and non-return globe valves has been compromised in some cases, based on feedback from plant personnel; steam-turbine components also have been damaged.

EPRI has established a committee on “Cracking and Disbonding of Hardfacing Alloys in Combined-Cycle Plant Valves” to dig into the details. The work, funded by several sponsors, began early this year. John Shingledecker (jshingledecker@epri.com), the technical manager for this program, said the project timeline is estimated at 14 months. The first formal review of industry experience is incorporated into the program for the upcoming EPRI Fossil Materials and Repair Program Technology Transfer Week, June 24-28, in Destin, Fla.

Owner/operators, valve manufacturers and service organizations, and other interested parties expect one outcome of the R&D effort will be a more reliable process for the bonding of stellite to discs, seats, and slides for valves subjected to steam temperatures approaching 1100F, as well as to rapid quenching caused by improperly operating desuperheaters and/or drain systems. The solution also may require changes to current industry inspection, operating, and maintenance procedures.

Industry experience suggests inspection of large steam valves at plants built during the late 1990s and early 2000s at the next hot-gas-path (HGP) or major inspection if this has not been done previously (see sidebar in this article). A visual inspection will confirm stellite liberation, dye penetrant testing will reveal cracking not visible with the naked eye, and a straight-beam ultrasonic examination will identify disbonding.

But before opening your valves, be sure to have a game plan for repair or replacement in case you find damage. Failure to plan ahead could significantly add to your outage schedule. Here are your options if damage is found:

  • Replace the existing valve with a new one.

  • Cut the valve out of the line and send it to the manufacturer or a qualified third-party shop for repair.

  • Repair the valve inline.

Owner/operators who have already faced repair/replace decisions suggest that you factor the following facts into your decision:

  • The lead time for new valves may extend beyond a year.

  • Shops capable of doing quality valve work and welding generally have a backlog.

  • Quality repairs are difficult to make inline because of preheat and access requirements. 

  • Field-service organizations with the requisite in-situ valve repair experience are extremely busy.

  • There is no industry standard for applying hardfacing. Manufacturers and repair firms have their own procedures and they should be qualified metallurgically before work begins on your valves. Plus, owner/operators are advised to carefully monitor repair work to the qualified written procedure.

Case history

The D11 steam turbine for a 2 x 1 7FA-powered combined cycle recently experienced an increase in HP-cylinder inlet pressure as well as a slight decrease in electrical output. Design steam conditions for the HRSGs were 1450 psig/1070F at the HP outlets and 450 psig/1067F at the HRH outlets. Lifetime operating hours totaled about 45,000, starts (mostly warm) 150.

Plant personnel began their investigation by following the recommendations of the OEM’s Technical Information Letter (TIL) 1629-R1, “Combined Stop and Control Valve Seat Stellite Liberation,” released Dec 31, 2010. The inspection team found that no stellite had been liberated from the valve seat; however, multiple cracks were found in the stellite inlay (Fig 1).

Important to note is that the two stellite alloys typically used for hardfacing of valve seats and discs are Stellite 6 and Stellite 21, trademarked products of Deloro Stellite Group. Since investigators did not know whether Deloro cobalt-based hardfacing alloys were used in the fabrication of these valves, the generic names Alloy 6 and Alloy 21 are used here.

This was not the first inspection of the combined stop and control valve (CSCV). It had been inspected during the 2009 major, shortly after the TIL was first published on Jan 30, 2009. The original TIL 1629 only called for visual (VT) and liquid-penetrant (PT) inspections. No cracking was found at that time. As noted above, Rev 1 of the TIL requires ultrasonic inspection, to identify any lack of bonding between the inlay and the base metal, if the unit has less than 50 starts.

Significance of the 50 starts: After that number of cycles, metallurgists believed any disbonding would have propagated to the edge of the inlay and could be identified with VT or PT. While the steamer had more than 50 starts at the time of the 2009 inspection, no PT indications were found at the edge of the hardfacing inlay. However, the ultrasonic inspection in 2012 revealed significant disbonding of the inlay.

A borescope inspection of the HP turbine revealed significant damage to diaphragms and rotating blades in several stages. During CSCV disassembly, metallic debris was found in the valve’s strainer (Fig 2). Analysis verified that its composition was consistent with the hardfacing alloy used on valve seats. Some debris had cut through the strainer and damaged HP turbine components.

1. Cracking in evidence is typical of that found in stellite seats for combined stop and control valves on steam turbines 2. Hardfacing debris was removed from the strainer for a combined stop and control valve 3. Delamination of the upstream seat ring (left) and downstream seat ring (right) for an HP stop valve is in progress

Based on these findings, plant management decided to check other high-temperature valves for damage. The inspection list included these eight valves on each unit:The next step was to identify the source of the hardfacing debris. A key clue: Operations personnel had reported that the HP stop valves were not sealing during shutdown. They were disassembled and the Unit 2 HP line stop was found with stellite missing from both the upstream and downstream seats (Fig 3). The Unit 1 HP line stop had its stellite in place, but showed signs of significant disbonding.

  • Three HP gates.
  • One HP non-return globe.
  • One CSCV.
  • One HRH gate.
  • One IP gate.
  • One cold reheat (CRH) check. 

Inspection results: Disbonding of hardfacing was identified on all HP and HRH valve seats; also on the seat and guide rails of the HP non-return globe valves. The IP and CRH valves showed no disbonding. Further investigation revealed that the hardfacing for the HP and HRH valves was applied using the Plasma Transferred Arc Welding (PTAW) process and for the HP non-return globes it was the Shielded Metal Arc Welding (SMAW) process.

Also, hardfacing on the HP and HRH gate-valve seats and discs was of bi-layered construction: An Alloy 21 buffer layer applied to the Grade 91 seat rings and an Alloy 6 finishing layer. The former is a low-carbon CoCrMo alloy with the AWS/ASME solid-wire filler-metal designation ERCoCr-E. It is characterized by reasonable ductility and metal-to-metal wear resistance at elevated temperatures. By contrast, Alloy 6 is a high-carbon CoCrW alloy with an AWS/ASME solid-wire designation of ERCoCr-A having improved metal-to-metal wear resistance at elevated temperatures.

Evaluation of the fracture surface raised concern that the failures were located in the Grade 91 base metal and might be similar to other creep-related dissimilar-metal failures found in Grade 91 piping (Fig 4). However, examination of the Grade 91 base metal revealed a tempered martensitic structure consistent with material that had been properly heat treated.The valve manufacturer’s service technician said that prior to the millennium, Alloy 6 typically was used for hardfacing of valve seats. But multiple disbonding incidents prompted his company to adopt the bi-layered approach. The thinking was that the improved ductility of Alloy 21 would minimize the risk of disbonding while the finishing layer of Alloy 6 would maintain a high degree of metal-to-metal wear resistance. Research revealed other valve manufacturers had similar issues with disbonding and they are using Alloy 21, stainless steel, or Inconel as buffer layers.

The heat-affected zone (HAZ) created by the deposition of hardfacing, while of a normal structure for Grade 91 material, was wider than normally would be expected given the thickness of the overlay. This indicated that relatively high heat inputs were used during the PTAW application of at least the buffer layer of Alloy 21. There was no evidence of creep damage in the Grade 91 HAZ.

Cracking that contributed to the disbonding of the hardfacing from the base metal developed near the interface between the valve seat and the stellite. It was caused largely by brittle fracture that had propagated through the Alloy 21 buffer layer. In some areas, the cracking propagated very close to, or along, the dissimilar-metal interface between the Grade 91 and Alloy 21.

Energy-dispersive X-ray spectroscopy (EDS) was performed on several samples to determine the chemical composition of the hardfacing layers. This analytical is used for elemental analysis of a material sample. The results showed high levels of iron dilution in the Alloy 21 buffer layer—ranging from 38% to nearly 70%.However, in these areas the fracture location appeared to be the result of the orientation of the brittle fracture rather than any unique “weakness” associated with the interface (weld fusion). Metallurgical evidence suggested that the dissimilar metal interface was not uniquely susceptible to the cracking and was only indirectly involved in the accumulation of damage (Fig 5).

4. Valve-seat fracture surface typically looks like this 5. Weld fusion line

Micro-hardness traverses also were taken to identify the hardness profiles of the materials involved. Grade 91 and Alloy 6 had hardness values within their expectedranges. But the Alloy 21 buffer-layer hardness, which ranged from 39 to 70 Rockwell C (most readings were above 50), was well outside the range expected for this material. Deloro Stellite says the hardness of its Stellite 21 typically is 27 HRC and can work-harden up to 40 HRC. 

Sidebar: Valves didn’t get the respect they deserved

The editors first learned of stellite delamination in a large valve designed for high-pressure (HP)/high-temperature steam service at the 2009 7F Users Group conference. But all the attention that incident received was a brief mention late in a long user presentation profiling the major inspection of a combined-cycle plant. More than 200 owner/operators were in attendance, yet no questions were asked about the issue—at least none the editors can recall—and it was quickly dismissed. Fig A  shows stellite liberated from the seat of a 20-in. hot-reheat block valve installed at that presenter’s plant and collected in the strainer for the steam turbine’s combined stop and control valve. more

Cobalt-based hardfacing alloys usually are considered for high-temperature applications because of their wear- and oxidation-resistant properties at elevated temperatures. These alloys rely on carbides for wear resistance and typically contain 24% to 32% chromium for oxidation resistance, plus 3% to 14% tungsten or molybdenum for added strength and for their carbide-forming ability.ranges. But the Alloy 21 buffer-layer hardness, which ranged from 39 to 70 Rockwell C (most readings were above 50), was well outside the range expected for this material. Deloro Stellite says the hardness of its Stellite 21 typically is 27 HRC and can work-harden up to 40 HRC.

Low-carbon hardfacing alloys, such as Alloy 21, which has 0.15% to 0.45% carbon, are reasonably ductile and provide metal-to-metal sliding wear resistance and cavitation erosion resistance. High-carbon alloys, like Alloy 6 (0.9% to 1.4% carbon), have limited ductility, but offer increased abrasion resistance. 
It would appear that the use of Alloy 21 as a buffer layer was an attempt to interpose between the Grade 91 base metal and the Alloy 6 wear layer a layer of more ductile material to better tolerate dynamic loads. However, the properties of the Alloy 21 buffer layer were altered significantly by changes in the weld-metal chemistry resulting from excessive dilution of the hardfacing during welding.

6. Correlation of buffer-layer hardnessFig 6 shows the correlation between hardness values and the level of iron dilution for the Alloy 21 buffer layer. While iron was used as the basis for calculating the percent dilution in this case, other key elements would have changed similarly. Note that as the level of dilution increases, the maximum hardness of the hardfacing deposit also increases. Thus the high rate of iron dilution into the Alloy 21 buffer layer of this valve seat produced a very hard layer with substantially reduced ductility.

As indicated above, investigators assumed that the intent of the Alloy 21 buffer layer was to provide a ductile layer under the final Alloy 6 layer. This is consistent with one of the recommendations from Stoody, a respected provider of hardfacing alloys (access “50 Hardfacing Tips” at http://victortechnologies.com/stoody): “Never put a tough ductile weld deposit on top of a harder, more brittle hardfacing deposit. Such deposits will spall, and lift off the part. The hardfacing alloy always should be applied on top of the more ductile material.”

Although it appears that the valve manufacturer attempted to do this by applying an Alloy 21 buffer layer, the level of iron dilution into the buffer layer apparently created the situation Stoody warned against—a softer deposit on top of a harder deposit, which resulted in disbonding of the hardfacing overlays.

To identify a possible driving force for crack growth, steady-state and transient heat-transfer and thermal stress analyses were performed using the finite-element method. The analyses included a postulated thermal shock (rapid cool-down) and a typical startup and shutdown thermal transient based on operational data provided by the owner/operator. Both the heat-up and thermal-shock stress analyses identified significant tensile axial stress at the Alloy 21/Grade 91 interface. This tensile stress is a possible driving force for crack growth.

The type of failure associated with the HRSG valve seats described here typically has not been observed in conventional fossil-fired steam-plant valves. For this case, it appears that the disbonding of hardfacing is caused by several conditions, including the following:

  • Higher operating temperatures than are normally experienced in conventional fossil-fired units, specifically 1050F to 1080F, versus 1005F. 

  • Higher rates of cycling, plus operating conditions capable of producing large quantities of condensate that contribute to thermal shock.

  • Material combinations not typically found in fossil-fired steam plants—such as Alloy 21 and Alloy 6 deposited on Grade 91.

  • Hardfacing layers with high hardness caused by excessive base-metal dilution into the hardfacing overlay.

Although the foregoing case history specifically deals with the valves from one manufacturer using composite Alloy 21/Alloy 6 hardfacing overlay, similar valve-seat failures have occurred in valves of various manufacturers not using buffer layers. Reports from several combined-cycle owner/operators leads investigators to believe the debonding described may be a generic issue.

Finally, if your inspection identifies disbonding, would you continue to operate or shut down to repair/replace the valve? This is not an easy decision to make for at least two reasons: First, the cause of disbonding is not yet fully established and, second, there is no data to predict the propagation rate of disbonding. 
If repairs are needed, or if you’re buying a new valve, it would be prudent to specify a limit on base-metal dilution into the first layer of hardfacing of between 10% and 20%, based on what investigators have learned to date. Minimizing base-metal dilution should reduce the hardness levels in the first layer of hardfacing and reduce the potential for disbonding. Qualify a prospective valve supplier or repair services provider by specifying a demonstration to prove their welding process can minimize dilution.

Whether you have experienced disbonding or not, be proactive regarding the review and modification of operating procedures to reduce the amount of condensate produced in superheater and reheater tube bundles during startup and shutdown. Verify, too, proper operation of attemperators to be sure excess water is not entering the steam path. Check your drain system to assure any condensate formed is being removed quickly and completely. CCJ