17 urn:lsid:arphahub.com:pub:8E638694-B4E0-570A-856A-746FF325BF6B Research Ideas and Outcomes RIO 2367-7163 Pensoft Publishers 10.3897/rio.2.e10714 10714 6426 PhD Project Plan Studying the effect of Ruthenium on High Temperature Mechanical Properties of Nickel Based Superalloys and Determining the Universal Behavior of Ruthenium at Atomic Scale with respect to alloying elements, Stress and Temperature Dasari Sriswaroop sriswaroopd@gmail.com ‡ Former graduate student at University of Florida, Gainesville, United States of America Former graduate student at University of Florida Gainesville United States of America

Corresponding author: Sriswaroop Dasari (sriswaroopd@gmail.com).

Academic editor:

2016 12 10 2016 2 e10714 F072F801-5423-58CB-861C-1C1F9B7ADE71 160336 04 10 2016 Sriswaroop Dasari This is an open access article distributed under the terms of the Creative Commons Attribution License 4.0 (CC-BY), which permits unrestricted use, distribution, and reproduction in any medium, provided the original author and source are credited. Ruthenium superalloy mechanical properties thermomechanical processing creep proposal Significance

The present researchers in material science design a suitable material to the given conditions based on the past knowledge and experiences with different alloys studied till date. It has been mostly trial and error design. This proposal suggests a plan to understand the universal behavior of every chemical element so that we shall be able to identify the limit of such element in the given application. Such study should not be limited to ruthenium but has to be extended to every chemical element. Ruthenium enhances the mechanical properties by quantities in a way that they had to be classified as fourth generation superalloys (Koizumi et al. 2004). Nevertheless it consumes a huge amount of time and work to understand the universal behavior of Ru. So, let’s take the first step by trying to understand the role of Ru in Ni based superalloys. This proposal is designed not only to study the universal behavior but it also tries to understand the feasibility of such study. To do this, we will need a complete superalloy manufacturing setup right from melting furnace to metal working equipment. The proposal also requires several machines that can test the mechanical properties. Different samples are prepared by changing composition and/or heat treatments. Microstructures and mechanical properties of different samples will be studied to find a correlation between percentage of ruthenium, microstructure and the properties. Such study can lead to a good understanding of how ruthenium affects the microstructure and properties which can lead to designing the right quantity of Ruthenium for an alloy with specific composition.

 Objectives

1. Identification of the role of Ruthenium as an alloying element in the modification of microstructure and mechanical properties of superalloys.

2. Extension of the study to different compositions so as to understand the way ruthenium behaves when certain chemical elements or conditions are imposed.

3. Feasibility of the study of universal behavior of a certain chemical element.

4. Extension of the same studies to all chemical elements by establishing a standard that has to be followed to perform such research.

5. Feasibility of extension of such research not only to various fields in materials science but also to different branches of science itself.

 Overview of Relevant Literature

The highly beneficial qualities of ruthenium to superalloys has been discovered very recently. Since then, many researchers have tried to understand the role of ruthenium but were able to make intermediary conclusions that are directly understood from their experiments. Atomic scale conduct of Ru has not been completely understood. The current understanding of ruthenium as per available literature till now goes as follows:

Ruthenium helps in producing a microstructure with smaller and more regular γ’ and denser dislocation structure at γ/ γ’ interface (Pyczak et al. 2009, Tan et al. 2011).

Ruthenium suppresses or at least doesn’t affect the tendency of the alloy to form topologically closed pack phases (TCP), (Sato et al. 2006, Tan et al. 2011, Tsuno et al. 2008)

While it preferentially partitions to γ, it increases the tendency of the elements Re, W, Mo, Cr, Co to partition to γ’, the so called reverse partitioning (Yokokawa et al. 2004).

It promotes square dislocation networks and change of γ/γ’ misfit which is beneficial to the mechanical properties of superalloys (Tan et al. 2011).

 Experimental Plan and Procedures a. Design of ingots

Consider the Ni-based superalloy TMS 138 which has the composition shown in Fig. 1 (National Institute for Materials Science and Ishikawajima-Harima Heavy Industries co., Ltd 2006). Since the aim of this proposal is to study ruthenium, all specimen compositions derived from TMS 138 will have different quantities of ruthenium. First, let’s consider the alloy that has only base metal and ruthenium (Sl. No. 1 in Table 1) and then keep on adding the other elements in equal amounts which would make them high entropy alloys. It might be trickier if we use an alloy that has many grain boundary strengtheners like C, B, Zr, Hf. If we use these strengtheners in equal amounts as of other elements, especially C, B form brittle compounds with the alloying elements and thus largely deteriorate the mechanical properties. So, TMS 138 is chosen which has only one grain boundary strengthener, Hf. The first nine specimen compositions are based on only the elements present in TMS 138 but not on atomic percentages of each element. The next nine specimen ingots will be prepared such that both the elements and their atomic percentages are taken into account. Compositions for these nine samples are designed in a way that they reflect the atomic percent ratios with respect to Ru in the original TMS 138. So, the last ingot will be TMS 138 itself. We shall prepare the ingots according to the compositions shown in Tables 1, 2 using investment casting technique (all numbers are in atomic percentages).

For comparison, all the 18 ingots in Table 1 have to be re-prepared without ruthenium which gives 17 more ingots to study. The differences in microstructure and mechanical properties between the ingot that has ruthenium and the ingot that has the same composition without ruthenium have to be noted down. Ingots without ruthenium content has the composition shown in Table 2 . While the first nine ingots in Table 2 (19-27) remain as high entropy alloys, the next eight ingots (28-35) have their atomic percentages normalized with respect to the Ni content in TMS 138.

 b. Thermomechanical processing

Now thermomechanical processing is performed on all samples (five from each ingot) to different strains/temperatures/times. All the samples must be first solution treated (ST) but the temperature will vary with composition. After solution treatment, samples undergo different amount of cold working, 0%, 20%, 40%. It is followed by aging treatments to several tens of degrees below ST temperature. Dual aging and grain boundary engineering can also be performed depending on the performance of the samples with temperature. A sample heat treatment schemes on any of the ingots may look as follows:

ST to 1150 C/12hrs + air quench

Cold working of sample using a rolling mill where its thickness is decreased by 20%

Aging to 870 C/24hrs + air quench

 c. Mechanical Testing

Mechanical testing of the samples will be carried out using hardness tester and creep testing equipment. Hardness tests can be done by using Rockwell microhardness tester. Creep tests have to be performed over a range of temperatures and stresses for at least 500hrs to assess the role of ruthenium. Possible creep testing conditions for many ingots can be as follows:

850 C/490MPa

950 C/275MPa

950 C/350MPa

1000 C/175MPa

1100 C/140MPa

All the creep tests will be performed in only one crystallographic direction, say <001> so that we shall be observing the mechanical behavior in one direction in all samples.

 d. Microstructural Characterization and Electron Dispersive Spectrometry

As the microstructural evolution has to be studied, microstructures have to be taken before and after every single treatment on the sample. Microstructures of all samples must be recorded using a Scanning electron microscope (SEM). Every microstructure have to be studied in terms of grain size, distribution and percentage of precipitates. Focus should be more on comparison between the ingots that have similar compositions but with and without ruthenium. Current technology allows us to perform in-situ SEM during heat treating and it will be utilized wherever necessary and appropriate. Samples from creep tests have to be electrochemically polished and observed under a Transmission electron microscope to study the γ’ and precipitate morphology in the sample. Electron dispersive spectrometry (EDS) will be performed on all samples except on HEA10 to study the precipitates and partitioning of alloying elements to γ, γ’ and topologically closed pack phases (TCP). As the alloy does not contain elements with atomic number less than six, EDS is a non-destructive, quick and effective technique for composition analysis.

 Results and Statistical Analysis of Results

Every feature of microstructure and every property of the material speaks about the role of the alloying elements. But due to time constraint, all the features of microstructures but only certain important properties of the material, hardness and creep rupture life will be determined under this proposal. The mechanical properties of six samples taken from RHEA1 ingot that have different thermomechanical processing history can be as shown in Table 3 and all the features of microstructure are tabulated in Fig. 2. Table 3 shows that 12 samples are required from each ingot and therefore, a total of 420 samples will be studied under this proposal.

Statistical analysis of the data obtained in Table 3 and Fig. 2 will be quite useful to this proposal. As we are looking for abnormal behavior in the alloy due to ruthenium content, statistical analysis using Stata (Hartman 2000, Leeper 2007) and ADMB softwares can evaluate the reliability and authenticity of obtained results. We shall design a C++ program that can represent the nature of results obtained through the experiments. Input feed to the program consists of hardness, creep test results and microstructural features from the research in past publications and from the present experiments. Thus we will be able to identify the aberrations from conventional behavior and hence the role of ruthenium.

 Discussion

From the observations, metals may be ranked in an ascending order similar to an electrochemical series. This series tells how a metallic element behaves when a certain element/group of elements are present in the alloy. I suppose it is impossible to anticipate the role of ruthenium in the alloy without performing the actual experiments. However, this proposal gives an estimate of the quality and quantity of work and time needed for such study and the appropriate methods that are to be followed to achieve a good understanding of ruthenium. The results act as a database to determine the right quantity of ruthenium to a given composition and a given set of operating conditions. The proposal also acts as a guide for experimentation to understand the universal behavior of other alloying elements like Cr, Co, Hf, Mo, W etc.

 Possible Extensions

The research of understanding the universal behavior of Ruthenium can be further extended to every other alloying element Ni, Cr, Co, Hf, Mo etc. so that there will be a complete understanding of what a certain element can do with its partner elements and imposed conditions. This proposal will act as the first step towards designing ideal compositions for a specific application.

 Timeline

To reduce the time for experimentation, this work will be done by collaborating with one more researcher belonging to a different research organization. The work at the other institute consists of creep testing of half the samples i.e. 210 samples. As this proposal requires heavy logical thinking, understanding and knowledge of the subject rather than just experimentation, it requires four graduate students and a period of six years. The timeline for the proposal follows Table 4.

 Acknowledgements

I am thankful to all of my teachers especially to Dr. John. J. Mecholsky, University of Florida, USA for the guidance on writing a research proposal.

 References Hartman Julia http://bama.ua.edu/~jleeper/627/choosestat.html Koizumi Y. Osawa M. Kobayashi T. Yokokawa T. Zhang J. Harada H. Aoki Y. Arai M. 2004 Superalloys 35-43 https://doi.org/10.7449/2004/superalloys_2004_35_43 10.7449/2004/superalloys_2004_35_43 Leeper James D. http://www.ats.ucla.edu/stat/mult_pkg/whatstat/choosestat.html Science National Institute for Materials Ishikawajima-Harima Heavy Industries co. Ltd 2006 Fourth generation nickel base single crystal superalloy TMS-138/138A 1-6 http://sakimori.nims.go.jp/catalog/TMS-138-A.pdf Pyczak Florian Neumeier Steffen Göken Mathias 2009 Influence of lattice misfit on the internal stress and strain states before and after creep investigated in nickel-base superalloys containing rhenium and ruthenium Materials Science and Engineering: A 510-511 295 300 https://doi.org/10.1016/j.msea.2008.08.052 10.1016/j.msea.2008.08.052 Sato Atsushi Harada Hiroshi Yokokawa Tadaharu Murakumo Takao Koizumi Yutaka Kobayashi Toshiharu Imai Hachiro 2006 The effects of ruthenium on the phase stability of fourth generation Ni-base single crystal superalloys Scripta Materialia 54 9 1679 1684 https://doi.org/10.1016/j.scriptamat.2006.01.003 10.1016/j.scriptamat.2006.01.003 Tan X. P. Liu J. L. Jin T. Hu Z. Q. Hong H. U. Choi B. G. Kim I. S. Jo C. Y. 2011 Effect of ruthenium on high-temperature creep rupture life of a single crystal nickel-based superalloy Materials Science and Engineering: A 528 8381 8388 https://doi.org/10.1016/j.msea.2011.07.075 10.1016/j.msea.2011.07.075 Tsuno N. Kakehi K. Rae C. M.F. Hashizume R. 2008 Effect of Ruthenium on Creep Strength of Ni-Base Single-Crystal Superalloys at 750 °C and 750 MPa Metallurgical and Materials Transactions A 40 2 269 272 https://doi.org/10.1007/s11661-008-9744-6 10.1007/s11661-008-9744-6 Yokokawa T. Saeki H. Fukuyama Y. Yoshida T. Harada H. 2004 Superalloys 859-866 https://doi.org/10.7449/2004/superalloys_2004_859_866 10.7449/2004/superalloys_2004_859_866

Chemical composition of TMS 138 alloy.

All features of the microstructures from the six samples taken before and after creep tests

Design of alloy compositions containing ruthenium. *RHEA – High entropy alloy with Ruthenium, *RCA – Conventional alloy with Ruthenium

Sl. No. Alloy Referred to as
1. 50Ni – 50Ru (RHEA1)
2. 33.34Ni – 33.33Co – 33.33Ru (RHEA2)
3. 25Ni – 25Co – 25Cr – 25Ru (RHEA3)
4. 20Ni – 20Co – 20Cr – 20Al – 20Ru (RHEA4)
5. 16.67Ni – 16.66Co – 16.67Cr – 16.66Al – 16.67Ta – 16.67Ru (RHEA5)
6. 14.28Ni – 14.28Co – 14.28Cr – 14.28Al – 14.28Ta – 14.28Mo - 14.28Ru (RHEA6)
7. 12.5Ni – 12.5Co – 12.5Cr – 12.5Al – 12.5Ta – 12.5Mo – 12.5Re – 12.5Ru (RHEA7)
8. 11.11Ni – 11.11Co – 11.11Cr – 11.11Al – 11.11Ta – 11.11Mo – 11.11Re – 11.11W –11.11Ru (RHEA8)
9. 10Ni – 10Co – 10Cr – 10Al – 10Ta – 10Mo – 10Re – 10W – 10Hf – 10Ru (RHEA9)
10. 97Ni – 3Ru (RCA1)
11. 88.88Ni – 8.31Co – 2.77Ru (RCA2)
12. 85.12Ni – 7.98Co – 4.25Cr – 2.66Ru (RCA3)
13. 80.8Ni – 7.56Co – 4Cr – 7.56Al – 2.52Ru (RCA4)
14. 75.52Ni – 7.05Co – 3.77Cr – 7.05Al – 6.6Ta – 2.36Ru (RCA5)
15. 72.96Ni – 6.84Co – 3.64Cr – 6.84Al – 6.38Ta – 3.19Mo - 2.28Ru (CAR6)
16. 69.12Ni – 6.48Co – 3.02Cr – 6.48Al – 6.04Ta – 3.02Mo – 5.4Re – 2.16Ru (RCA7)
17. 65Ni – 6.09Co – 3.24Cr – 6.09Al – 5.68Ta – 2.84Mo – 5.07Re – 6.09W – 2.03Ru (RCA8)
18. 63.7Ni – 5.8Co – 3.2Cr – 5.9Al – 5.6Ta – 2.8Mo – 5Re – 5.9W – 0.1Hf – 2Ru (TMS 138)

Design of alloy compositions that does not contain ruthenium. *HEAX0 – High entropy alloy with zero ruthenium, *CAX0 – Conventional alloy with zero ruthenium

Sl. No. Alloy Referred to as
19. 100Ni (HEA10)
20. 50Ni – 50Co (HEA20)
21. 33.34Ni – 33.33Co – 33.33Cr (HEA30)
22. 25Ni – 25Co – 25Cr – 25Al (HEA40)
23. 20Ni – 20Co – 20Cr – 20Al – 20Ta (HEA50)
24. 16.67Ni – 16.66Co – 16.67Cr – 16.66Al – 16.67Ta – 16.66Mo (HEA60)
25. 14.28Ni – 14.28Co – 14.28Cr – 14.28Al – 14.28Ta – 14.28Mo – 14.28Re (HEA70)
26. 12.5Ni – 12.5Co – 12.5Cr – 12.5Al – 12.5Ta – 12.5Mo – 12.5Re – 12.5W (HEA80)
27. 11.11Ni – 11.11Co – 11.11Cr – 11.11Al – 11.11Ta – 11.11Mo – 11.11Re – 11.11W – 11.11Hf (HEA90)
28. 97Ni – 3Co (CA10)
29. 88.88Ni – 8.31Co – 2.77Cr (CA20)
30. 85.12Ni – 7.98Co – 4.25Cr – 2.66Al (CA30)
31. 80.8Ni – 7.56Co – 4Cr – 7.56Al – 2.52Ta (CA40)
32. 75.52Ni – 7.05Co – 3.77Cr – 7.05Al – 6.6Ta – 2.36Mo (CA50)
33. 72.96Ni – 6.84Co – 3.64Cr – 6.84Al – 6.38Ta – 3.19Mo - 2.28Re (CA60)
34. 69.12Ni – 6.48Co – 3.02Cr – 6.48Al – 6.04Ta – 3.02Mo – 5.4Re – 2.16W (CA70)
35. 66Ni – 6.29Co – 3.44Cr – 6.29Al – 5.78Ta – 2.34Mo – 5.17Re – 6.19W – 0.3Hf (CA80)

Hardness and creep rupture life of six samples from RHEA1 ingot. *RHEA10X – Sample from RHEA1 ingot with a thermomechanical history represented by X, **ST1 – Solution Treatment temperature for the specific alloy, ***A1, A2 – Aging treatments specific to that alloy

Sample Name ST Cold work Aging Hardness(hν) Time to 1% Creep Strain
950C/350MPa 1100C/140MPa
RHEA101* ST1** 0 A1***
RHEA102 ST1 20 A1
RHEA103 ST1 40 A1
RHEA104 ST1 0 A2
RHEA105 ST1 20 A2
RHEA106 ST1 40 A2

Timeline for the proposal

Task Time required
Preparation of 34 different ingots with varying compositions 1 year
Sample cutting for various tests 8 months
Thermomechanical processing 6 months
Mechanical testing (assuming at least 2 creep testers) 3 years
Microstructural Characterization 6 months
Interpretation and co-relation of results 4 months