SciELO - Scientific Electronic Library Online

 
vol.15 issue4Manufacturing polycrystalline pellets of natural quartz for applications in thermoluminescence dosimetryInfluence of thermal treatment on bentonite used as adsorbent for Cd, Pb, Zn retention from mono-solute and poly-solute aqueous solutions author indexsubject indexarticles search
Home Pagealphabetic serial listing  

Materials Research

Print version ISSN 1516-1439

Mat. Res. vol.15 no.4 São Carlos July/Aug. 2012 Epub July 03, 2012

http://dx.doi.org/10.1590/S1516-14392012005000072 

Crack propagation under constant amplitude loading based on an energetic parameters and fractographic analysis

 

 

Mohamed Benguediab*; Benattou Bouchouicha; Zemri Mokhtar; Mohamed Mazari

Laboratory and Reactive Systems, Department of Mechanical Engineering, University of Sidi Bel Abbes, Algeria

 

 


ABSTRACT

The crack propagation behavior in a 2024 T351 Aluminum Alloy under constant amplitude loading has been studied. This study is complemented by quantitative microfractographic observations and energetic analysis. The obtained results under constant amplitude fatigue tests show that different crack propagation stages can be identified and correlated with the evolution of the characteristic features. In another hand, the energetic analysis shows that there is a discontinuous crack growth at low growth rates as against a cycle by cycle growth mechanism at high growth rates.

Keywords: fatigue crack growth, energy dissipated, features, dimples, striations


 

 

1. Introduction

Fatigue crack growth resistance of a material depends upon a number of factors, such as its composition, mechanical properties and heat treatment conditions, external loading and the ambient environment.

Understanding of the mechanisms governing fatigue crack has made significant advances since the Paris law proposed about 40 years ago1.

This relationship can show several stages separated by transitions (Figure 1)2-4. Predominant micro structural size, the ambient environment and the frequency of solicitation can modify the behavior of the crack growth curves (da/dN vs δK) and the transitions3.

 

 

There exists a threshold of non propagation under which a preexistent long crack does not grow5. The value of δKth is a function of the load ratio R and the environment3,5.

For medium crack growth rates ((10-8 < da/dN < 10-5) m/cycle for aluminum alloys), the relationship between da/dN and δK is characterized by independent constant slope of the load ratio R.

This stage is also characterized by the existence of fatigue striations whose interval can be directly correlated with macroscopic crack growth rate6-8. In this stage, the crack growth behavior is characterized in considering the effect of crack closure effect9.

For crack growth rates greater than 10-6 m/cycle, we notice an increasing in the crack growth rate as we approach the static rupture conditions10.

In Ranganathan work, an energetic approach11,12 based on the theoretical model of Weertman12 permits a better comprehension of mechanisms of propagation with a possible correlation between macroscopic and microscopic mechanisms.

This paper presents the results of a quantitative analysis of the characterized features with respect to different parameters governing the crack propagation behavior completed by an energy analysis.

 

2. Experimental Details

The study was conducted on the high strength aluminum alloy 2024 T351. Nominal composition and mechanical properties are given in Table 1 and 2.

 

 

 

 

The tests are conducted on compact tension specimens 12 mm thick and 75 mm wide, with the crack growth in the LT orientation.

The constant amplitude tests at five R ratios ( 0,01; 0,10; 0,33; 0,54 and 0,70) were carried out initially to characterize the material behavior.

All the tests were carried out under computer control at 20 Hz in ambient air and at selected crack length, the evolution of the crack mouth opening displacement δ (measured by a clip gage) and the differential displacement δ' with respect to the load P were recorded on a XY plotter at a frequency of 0,2 Hz. δ' is defined by (Equation 1):

Where α is the specimen compliance at a particular crack length. The measurements were carried out during one cycle for constant amplitude tests and during one block for a reduced spectrum loading.

Typical δ vs P and δ' vs P diagrams for constant amplitude loading are given in Figure 2.

 

 

Crack opening load Pop was measured at the beginning of the horizontal portion on δ' vs P diagram13.

The Hysteresis energy per cycle, Q, was measured numerically integrating the area under the load versus amplified displacement diagrams measured under the loading line of the specimen. The specific energy US is defined as (Equation 2):

Where "B" is the thickness of specimen and "da/dN" the crack growth rate.

After the tests, the broken surfaces were examined under scanning microscope, at different magnifications varying from 200 to 10000 to identify and quantify different fractographic features. A method for quantitative analysis of fatigue fracture surfaces is proposed, the following technique method presented in14,15 is used.

In the present study the relative amount on the main fractographic feature are:

  • Pseudo-cleavage16 or « fish-bone structure » which is encountered at low K values this structure differs from the cleavage by the facet that crack path differs slightly from the defined crystallographic planes (Figure 3a).
  • Striations 1 (S1), which are classical ductile striations17 which can be correlated to the macroscopic crack growth rate (Figure 3b).
  • Striations 2 (S2), they are more pronounced markings than striations 1 and the spacing between these striations seem to be independent of the macroscopic crack growth rate(Figure 3b)
  • Dimples 1 (D1) which represent decohesions observed at low K values (Figure 3b)
  • Dimples 2 (D2) which are classical dimples observed at relatively high K values.

 

3. Experimental Results

The evolution of da/dN with respect to Kmax and δK for five different R ratios is given in Figures 4a and 4b. The stress intensity factor δK and Kmax are determined according to ASTM standards18.

The results are comparable to those obtained by Wanhill3 for the same material. The rates obtained at R = 0.01 and R = 0.1 are similar. We noted that on the Figure 4a and 4b, the existence of transitions (T1, T2, T3) characterized by a change of on the curves when the relation da/dN vs δK is different. The different transitions observed are identified in Table 3.

 

 

The analysis of these results proves the existence of four domains of cracks19.

3.1. Results of quantitative fractographic analysis

In a first approach, only two classes of features were considered: a first one including the pseudo-cleavage areas and striations and a second on including D1 and D2 dimples.

Typical results are given in Figure 5. It can notice at low Kmax values almost the entire surfaces is occupied by pseudo-cleavage facets. At Kmax values corresponding to T1 transition, dimples appear and their relative percentage increase with Kmax until reaching a maximum.

 

 

With further increasing Kmax values this percentage decreases before increasing abruptly close the final rupture. This evolution of dimple percentage suggests that D1 and D2 result from two different mechanisms. This final increase of this percentage can be correlated with the T3 transition in the crack growth curves.

To get more precise information a second approach for the quantitative analysis of the fracture surfaces were developed considering three different fractures striations, dimples D1 and D2.

A typical example of the results obtained at R = 0.10 and R = 0.70 is given in Figure 6a and 6b.

At R = 0.10, the percentage of striations reaches a top value for Kmax values ranging from 12 to 28 MPa i.e from T1 to T3.

At R = 0.70, the evolution of the percentage of striations is similar that observed at R = 0.10, but quantitative differences exist.

3.2. Energetic analysis

The results are analyzed in terms of the energy parameters. The evolution of the crack growth rate with respect to the energy dissipated per cycle Q for different R ratios is presented in Figure 7.

 

 

In this figure, we show the existence of two distinct stages.

At high growth rates values, the relationship between da/dN and Q is linearly and can be expressed as follow (Equation 3):

with A above 1,8 10-4

For lower growth rates values, the relationship between da/dN and Q can represent by a power law of the type (Equation 4):

With

B = 2, 22 10-5

n = 3, 80

The relationship between the specific energy US and Kmax is shown in Figure 8. In this figure, it can be seen that the specific energy US reaches a minimum level called Ucr at about 2,17 × 105 J.m-2 when the stress intensity factor reaches a critical value Kmax = 17 MPa, value comparable to the value of transition T2 observed in the curves of propagation (see Figures 4a and 4b). The fratographic analysis20 shows that this change behavior can be associated to step by step mechanism at low growth the crack growth mechanism was characterized by striation formation during for each cycle where the specific energy was constant21.

 

 

4. Conclusion

Fractographic observations of the fatigue fracture surfaces in the case of high strength aluminum alloy 2024-T351 and their quantitative analysis completed by an energetic parameters analysis lead to the following conclusions:

  • The evolution of the typical fractographic features has been correlated to the different propagation regimes which are separated by characteristic transitions. Moreover, the influence of the load ratio R and the maximum stress intensity factor Kmax is taken into account by the analysis method.
  • Most aspects of crack growth mechanism can be explained by the energetic analysis.

The behavior for the material was attributed a crack advances step by step mechanism for lower growth rates and at high growth rates, the crack growth mechanism was characterized by striation formation during for each cycle where the specific energy was constant.

 

References

1. Paris PC and Erdogan F. A critical analysis of crack propagation laws. Journal of Basic Engineering. 1963; 85:528-534. http://dx.doi.org/10.1115/1.3656900        [ Links ]

2. Yoder GR, Cooley LA and Crooker TW. On microstructural control of near-threshold fatigue crack growth. Scripta Metallurgica. 1982; 16:1021-1025. http://dx.doi.org/10.1016/0036-9748(82)90448-3        [ Links ]

3. Wanhill RJH. Low stress intensity fatigue crack growth in 2024-T3 and T351. Engineering Fracture Mechanics. 1988; 30(2):233-260. http://dx.doi.org/10.1016/0013-7944(88)90227-5        [ Links ]

4. Grinberg NM. Stage II fatigue crack growth. International Journal of Fatigue. 1984; 6(4):229-242. http://dx.doi.org/10.1016/0142-1123(84)90054-9        [ Links ]

5. Klesnil M and Lukas P. Effect of stress cycle asymmetry on fatigue crack growth. Materials Science and Engineering. 1972; 9:231-239. http://dx.doi.org/10.1016/0025-5416(72)90038-9        [ Links ]

6. Pelloux RMN. Mechanism of formation of ductile fatigue striations. Transactions of the American Society of Metals Quarterly. 1969; 62:281.         [ Links ]

7. Laird C. The influence of metallurgical structure on the mechanisms of fatigue crack propagation. ASTM STP. 1967; 415:131-168.         [ Links ]

8. Nix KJ and Flower HM. To use of Electron Optical techniques in the study of fatigue in High strength aluminum alloy 7090. In: Sherraft F and Sturgeon JB. Materials, Experimentation and Design in Fatigue. Surrey: Westbury House Pub; 1979. p. 85.         [ Links ]

9. Elber W. The significance of crack closure. ASTM STP. 1971; 486:230-242.         [ Links ]

10. Forman RG, Kearney VE and Engle RM. Numerical analysis of crack propagation in cyclic-loaded structures. Journal of Basic Engineering. 1967; 89:459-464. http://dx.doi.org/10.1115/1.3609637        [ Links ]

11. Ranganathan N. Contribution au développement d'une approche énergétique à la propagation d'une fissure de fatigue. [Thesis]. Poitiers: University of Poitiers; 1985.         [ Links ]

12. Weertman J. Theory of fatigue crack growth based on a BCS crack theory with work hardening. International Journal of Fracture. 1973; 9(2):125-131. http://dx.doi.org/10.1007/BF00041854        [ Links ]

13. Kikukawa M, Jono M and Hora H. Fatigue crack propagation and closure behavior under plane strain condition. International Journal of Fracture. 1977; 13:699-701. http://dx.doi.org/10.1007/BF00017303        [ Links ]

14. Ranganathan N, Benguediab M, Henaff G and Adiwijajanto F. Quantitative fracture surface analysis of fatigue crack propagation under variable loading. In: Masters JE, editor. Fractography of Modern Engineering Materials. ASTM STP 1203; 1993. p. 71-94.         [ Links ]

15. Underwood EE and Starke Junior EA. Quantitative stereological methods for analyzing important microstructural features in fatigue of metals and alloys. ASTM STP 675; 1979. p. 633-682.         [ Links ]

16. Herztberg RW and Mills WJ. Character of fatigue fracture surface micromorphology in ultra low growth rate regime. ASTM STP 600; 1976, p. 220-34.         [ Links ]

17. Bates RC and Clark WG. Fractography and fracture mechanics. Transactions of American. Society for Metals. 1969; 62:380-388.         [ Links ]

18. American Society for Testing and Materials - ASTM. E 647-96: Standard test method for measurement of fatigue crack growth rates. ASTM; 1999. Annual Book of ASTM Standards. v. 03.01.         [ Links ]

19. Benguediab M. Etude de la propagation des fissures de fatigue sous spectres de chargement réduits. [Thesis]. Poitiers: University of Poitiers; 1989.         [ Links ]

20. Ranganathan N, Bouchet B and Petit J. Fractography aspects of the effects of environment on the fatigue crack propagation mechanism in a high strength aluminum alloy. ASTM STP 948; 1987. p. 424-446.         [ Links ]

21. Ranganathan N. Analysis of fatigue crack growth in terms crack closure and energy. ASTM STP 1343; 1999, p. 14-38.         [ Links ]

 

 

Received: March 8, 2012
Revised: April 16, 2012

 

 

* e-mail: benguediab_m@yahoo.fr