Microstructural Evolution of Dissimilar Metal Welds ......Microstructural Evolution of Dissimilar...

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Michelle Kent, Sean Orzolek, Dr. John N. DuPont Lehigh University, Materials Science and Engineering Microstructural Evolution of Dissimilar Metal Welds Involving Grade 91 Steel Objective The objective is to understand the microstructural evolution across the weld interface of dissimilar metal welds involving grade 91 steel. Background Dissimilar metal welds (DMWs) join two alloys of different compositions, resulting in a high-energy interface prone to failure due to differences in chemical potential, coefficient of thermal expansion, and carbon diffusivity across the interface [1]. Power plants use hundreds of DMWs to join low-cost ferritic steels used in environments up to 550°C with more expensive austenitic metals that withstand the high- temperature and high-pressure environment of steam vessels [1,2]. DMW failure in welds involving grade 91 steel has been shown to occur within a 1-3 μm ferritic band that forms along the fusion line in the base metal. Problem Statement Hundreds of dissimilar metal welds (DMWs) are used throughout every fossil and nuclear power plant. DMWs involving grade 91 steel have been found to fail along the fusion line well before their 30 year expected creep lifespans. DMW failures causing power plant shutdown can cost up to $850,000 per day [2]. Alloy 625/Grade 91 GTAW Welds As welded condition Post weld heat treated (PWHT), 1 hour at 760 °C 1-hr PWHT at 760 °C, aged 6000 hours at 625 °C Experimental Methods DICTRA Diffusion Modeling Microhardness Indentation Testing Light Optical Microscopy (LOM) Scanning Electron Microscopy (SEM) References 1. William Gordon Clark, John. (2015). Investigating chemical and microstructural evolution at dissimilar metal welds. EngD Thesis, University of Nottingham. 2. DuPont, J. N. (2012). Microstructural evolution and high temperature failure of ferritic to austenitic dissimilar welds, International Materials Reviews, 57:4, 208-234, DOI:10.1179/1743280412Y.0000000006. 3. DuPont, John N, et al. Welding Metallurgy and Weldability of Nickel-Base Alloys. Wiley, 2009. 4. DuPont, J. N. (2016). Microstructural Characterization and Modeling of Dissimilar Weld Failures Involving Grade 91, Whitehall, PA: JND Metallurgical Consulting, LLC. Conclusions and Remarks Grade 91 steel softened with PWHT due to martensite tempering, while Alloy 625 hardened with PWHT and again with aging due to carbide and precipitate formation The carbide-free band is associated with failure Nanohardness indentation is being used to analyze the short-range hardness trends near the weld interface Figure 4. The high cooling rate of welding causes hard martensite to form in the base metal. After 1 hour PWHT, strain relaxes and the hardness decreases as martensite tempers. Base Metal Figure 3. Microhardness indent traces taken across the DMW fusion line with a 5 g load and 30 μm spacing. Welds were tested as welded, 1 hour PWHT condition, and 6000 hour aged condition. In the base metal, the hardness decreases after 1 hour PWHT and remains constant after aging. In the weld metal, the hardness increases after 1 hour PWHT and again after 6000 hours of aging. Partially Mixed Zone Fusion Zone Heat Affected Zone Base Metal Location of Carbide-Free Region 500 μm Figure 2. DMW creep failure has been shown to occur within a narrow ferritic band along the fusion line. [4] Creep Voids Carbide Free Region FCC/BCC Interface Type I Carbides Figure 7. Hardness and simulated carbon concentration as a function of distance across the interface. A localized increase in hardness correlates with an increase in carbon concentration just inside the weld metal. Figure 5. M6C carbides are predicted to form after 1 hour PWHT at 760 °C. Ni3Nb precipitates are predicted to form after 6000 hours of aging at 625 °C. [3] Figure 6. M6C carbides and Ni 3Nb are predicted in alloy 625 according to the time transformation diagram. [3] Weld Metal Figure 1. Schematic cross section of a DMW. The location of the carbide free region is indicated. …………………………….. Acknowledgement s : Results

Transcript of Microstructural Evolution of Dissimilar Metal Welds ......Microstructural Evolution of Dissimilar...

Page 1: Microstructural Evolution of Dissimilar Metal Welds ......Microstructural Evolution of Dissimilar Metal Welds Involving Grade 91 Steel Objective ... • Dissimilar metal welds (DMWs)

Michelle Kent, Sean Orzolek, Dr. John N. DuPont

Lehigh University, Materials Science and Engineering

Microstructural Evolution of Dissimilar

Metal Welds Involving Grade 91 Steel

ObjectiveThe objective is to understand the microstructural evolution across the

weld interface of dissimilar metal welds involving grade 91 steel.

Background• Dissimilar metal welds (DMWs) join two alloys of different

compositions, resulting in a high-energy interface prone

to failure due to differences in chemical potential,

coefficient of thermal expansion, and carbon diffusivity

across the interface [1].

• Power plants use hundreds of DMWs to join low-cost

ferritic steels used in environments up to 550°C with more

expensive austenitic metals that withstand the high-

temperature and high-pressure environment of steam

vessels [1,2].

• DMW failure in welds involving grade 91 steel has been

shown to occur within a 1-3 µm ferritic band that forms

along the fusion line in the base metal.

Problem StatementHundreds of dissimilar metal welds (DMWs) are used throughout every fossil and nuclear power plant. DMWs involving grade 91 steel have been found to fail along the fusion line well before their 30 year expected creep lifespans. DMW failures causing power plant shutdown can cost up to $850,000 per day [2].

Alloy 625/Grade 91 GTAW Welds

•As welded condition

•Post weld heat treated (PWHT), 1 hour at 760 °C

•1-hr PWHT at 760 °C, aged 6000 hours at 625 °C

Experimental Methods• DICTRA Diffusion Modeling

• Microhardness Indentation Testing

• Light Optical Microscopy (LOM)

• Scanning Electron Microscopy

(SEM)

References1. William Gordon Clark, John. (2015).

Investigating chemical and microstructural

evolution at dissimilar metal welds. EngD

Thesis, University of Nottingham.

2. DuPont, J. N. (2012). Microstructural

evolution and high temperature failure of

ferritic to austenitic dissimilar welds,

International Materials Reviews, 57:4,

208-234,

DOI:10.1179/1743280412Y.0000000006.

3. DuPont, John N, et al. Welding Metallurgy

and Weldability of Nickel-Base Alloys.

Wiley, 2009.

4. DuPont, J. N. (2016). Microstructural

Characterization and Modeling of

Dissimilar Weld Failures Involving Grade

91, Whitehall, PA: JND Metallurgical

Consulting, LLC.

Conclusions and Remarks•Grade 91 steel softened with PWHT due to martensite tempering, while Alloy 625 hardened with PWHT and again with aging due to carbide and precipitate formation

•The carbide-free band is associated with failure

•Nanohardness indentation is being used to analyze the short-range hardness trends near the weld interface

Figure 4. The high cooling rate of

welding causes hard martensite to form

in the base metal. After 1 hour PWHT,

strain relaxes and the hardness

decreases as martensite tempers.

Base Metal

Figure 3. Microhardness indent traces taken across the DMW

fusion line with a 5 g load and 30 µm spacing. Welds were

tested as welded, 1 hour PWHT condition, and 6000 hour

aged condition. In the base metal, the hardness decreases

after 1 hour PWHT and remains constant after aging. In the

weld metal, the hardness increases after 1 hour PWHT and

again after 6000 hours of aging.

Partially

Mixed Zone

Fusion

Zone

Heat

Affected

Zone

Base

Metal

Location of

Carbide-Free

Region

500 µm

Figure 2. DMW creep failure has

been shown to occur within a narrow

ferritic band along the fusion line. [4]

Creep Voids

Carbide Free

Region

FCC/BCC

Interface

Type I

Carbides

Figure 7. Hardness and simulated carbon concentration

as a function of distance across the interface. A localized

increase in hardness correlates with an increase in carbon

concentration just inside the weld metal.

Figure 5. M6C carbides are predicted to form after 1 hour PWHT at 760 °C.

Ni3Nb precipitates are predicted to form after 6000 hours of aging at 625 °C. [3]

Figure 6. M6C carbides and Ni3Nb are

predicted in alloy 625 according to the

time transformation diagram. [3]

Weld Metal

Figure 1. Schematic cross section

of a DMW. The location of the

carbide free region is indicated.

……………………………..

Acknowledgements:

Results