AISI 304 Welding Fracture Resistance by a Charpy Impact Test with a High Speed Sampling Rate

The purpose of this study was to evaluate fracture resistance in AISI 304. The J-R curve was constructed from data, which resulted from an impact test by Charpy Impact machine equipped with high-speed sampling rate data acquisition equipment. The critical values of fracture resistance in fusion zones (FZ), high temperature heat affected zones (HTHAZ), low temperature heat affected zones (LTHAZ) and unaffected base metals (UBM) were obtained by calculation methods using some formulas and by graphical methods. Laboratory experiments demonstrated the relationships among the values of energy absorption along the impact test with the obstruction of dislocation movement due to the presence of chromium interstitial solute in all zones and chromium rich carbide precipitates in fusion zones and heat affected zones.


Introduction
The critical values of such fracture parameters are known as fracture resistance.Fracture resistance is the ability of a ductile material to accept load or deform plastically and resist fractures in the presence of cracks based on the Elastic Plastic Fracture Mechanics (EPFM) approach [1][2][3].J-R curves have been widely used to measure the fracture resistance, and their determination has been standardized in ASTM E 1820, which combines the testing and analysis procedures of E 813 and E 1152.The recommended specimen in the standard were fatigue pre-crack [C(T)] and [SE(B)] specimen.Load versus load line displacement were recorded by digital instruments or autographically by x-y plotter.The record of load versus displacement was used to determine crack length.Since Load P, displacement v and crack length have been estimated at each data point, referring to ASTM E 1820, J could be evaluated to construct J-R curves.
The procedure needs precise specimen preparation and high accuracy instruments to run.The overall J-R curve construction procedure was time consuming and costly.It was also not easy to implement.On the other hand, impact toughness tests evidently could be done at reasonable costs and have been developed for metals and non-metal testing with various purposes easily [4][5][6][7].Some studies have successfully determined J-R curves by applying the normalization method on Charpy Impact test data [2,[8][9][10].The normalization method, which uses the principle of load separation, has been introduced as the convenient way for J-R curve determination.The method related three variables, load P, displacement v, and crack length during the fracture process, which provides a prediction of any one among three variables from the other two.Using the normalization method, there were many studies that developed further techniques for J-R curve determination in order to overcome some difficult conditions such as: unavailability of crack length, displacement or load measurement [1,2].Other studies investigate the possibility to apply a Charpy V-notched (CVN) test to determine fracture toughness K IC and critical crack resistance values, J IC [11][12][13].Like the previous method, the basic concept of the crack length was proportional to the square of absorbed energy.Stainless steel is a metallic alloy consisting of at least 10.5% chromium (Cr) and 50% iron (Fe).There are various grades of stainless steel such as: Austenitic Stainless Steel, Ferritic Stain less steel, Martensitic stainless steel, duplex stainless steel and precipitation hardening stainless steel.Austenitic Stainless Steel is the most widely used due to its corrosion resistance, mechanical properties and economic value [14].As, in general, AISI 304 welding potentially faced crack problems, which were considered to be the most serious problems among a variety of physical defects.When there were some cracks in structural components, it could fail at a lower stress level than the ultimate strength of the material [1,2].Many failures have occurred as a result of fracture, even though the yield stress was not reached.
The main purpose of this study was to apply the previous findings on fracture resistance determination by the Charpy Impact Test to investigate fracture resistance profiles and fracture resistance critical values of American Iron and Steel Institute Standard 304 (AISI 304) welding.Charpy Impact machine equipped with high-speed sampling rate data acquisition equipment is expected to exhibit precisely the relation among the values of energy absorption along the impact test with the presence of chromium interstitial solute and chromium rich carbide precipitation.The relationships were suspected as important keywords in describing fracture resistance profile in each AISI 304 welding zone.When energy absorption along the impact test was increased, it very likely has a strong relationship with obstruction of dislocation movement by the presence of Cr as a dominant particle in AISI 304, which has a high hardness and yield strength even at high temperature.The formation of chromium carbides and its properties on AISI 304 welding also hamper the movement of dislocation.Both of these obstruction agents were suspected to be the cause of increased energy absorption capability of post welding AISI 304 through the length of Charpy Impact tests, and, finally, influence the fracture resistance profile.

Experimental Method
AISI 304 strip plate with the dimension of 1000 mm × 100 mm × 10 mm as shown in Figure 1 was used as a basic material for all necessary testing to investigate the values of AISI 304 welding fracture resistance.Composition of the basic material is presented in Table 1.
Metals 2017, 7, 543 2 of 14 to determine fracture toughness KIC and critical crack resistance values, JIC [11][12][13].Like the previous method, the basic concept of the crack length was proportional to the square of absorbed energy.Stainless steel is a metallic alloy consisting of at least 10.5% chromium (Cr) and 50% iron (Fe).There are various grades of stainless steel such as: Austenitic Stainless Steel, Ferritic Stain less steel, Martensitic stainless steel, duplex stainless steel and precipitation hardening stainless steel.Austenitic Stainless Steel is the most widely used due to its corrosion resistance, mechanical properties and economic value [14].As, in general, AISI 304 welding potentially faced crack problems, which were considered to be the most serious problems among a variety of physical defects.When there were some cracks in structural components, it could fail at a lower stress level than the ultimate strength of the material [1,2].Many failures have occurred as a result of fracture, even though the yield stress was not reached.
The main purpose of this study was to apply the previous findings on fracture resistance determination by the Charpy Impact Test to investigate fracture resistance profiles and fracture resistance critical values of American Iron and Steel Institute Standard 304 (AISI 304) welding.Charpy Impact machine equipped with high-speed sampling rate data acquisition equipment is expected to exhibit precisely the relation among the values of energy absorption along the impact test with the presence of chromium interstitial solute and chromium rich carbide precipitation.The relationships were suspected as important keywords in describing fracture resistance profile in each AISI 304 welding zone.When energy absorption along the impact test was increased, it very likely has a strong relationship with obstruction of dislocation movement by the presence of Cr as a dominant particle in AISI 304, which has a high hardness and yield strength even at high temperature.The formation of chromium carbides and its properties on AISI 304 welding also hamper the movement of dislocation.Both of these obstruction agents were suspected to be the cause of increased energy absorption capability of post welding AISI 304 through the length of Charpy Impact tests, and, finally, influence the fracture resistance profile.

Experimental Method
AISI 304 strip plate with the dimension of 1000 mm × 100 mm × 10 mm as shown in Figure 1 was used as a basic material for all necessary testing to investigate the values of AISI 304 welding fracture resistance.Composition of the basic material is presented in Table 1.The material was then welded by TIG with the welding specification as performed in Table 2.The material was then welded by TIG with the welding specification as performed in Table 2.In order to place the notch precisely in the fusion zones, high temperature heat affected zones, low temperature heat affected zones and unaffected base metals, microstructure observation by optical microscope with a magnification of 100× was conducted for each zone.The microstructure images of each zone and the distance of notches from the center of welding were shown in Figure 2a-d In order to place the notch precisely in the fusion zones, high temperature heat affected zones, low temperature heat affected zones and unaffected base metals, microstructure observation by optical microscope with a magnification of 100× was conducted for each zone.The microstructure images of each zone and the distance of notches from the center of welding were shown in Figure 2ad, respectively.Seven AISI 304 three points bending welded impact specimens for each zone with the dimensions of 55 mm × 10 mm × 10 mm were prepared using Electrical Discharge Machining (EDM) referring to the ASTM E 23-02a standard [13].The relative position notch from the center weld bead was presented in Figure 3. Seven AISI 304 three points bending welded impact specimens for each zone with the dimensions of 55 mm × 10 mm × 10 mm were prepared using Electrical Discharge Machining (EDM) referring to the ASTM E 23-02a standard [13].The relative position notch from the center weld bead was presented in Figure 3. Based on ASTM E 23-02a, Charpy Impact tests were conducted with a 300 Joules × 2 Charpy Impact machine equipped with a high-speed sampling rate data acquisition instrument (see Figure 4) in order to examine the energy absorption profile in each zone.The data acquisition instrument (manufactured by Advantech Corporation, Taipei, Taiwan) that consists of a S-type Load Cell, ADAM 3016 signal conditioner, and USB 4702-AE analog to digital converter (ADC) was set to record 45,000 samples per second.Fracture surface was observed by a Hitachi SU 3500 Scanning Electron Microscope (Tokyo, Japan) and Energy Dispersive X-ray Spectroscopy, which has the ability to magnify 10-300,000× with a depth of field of 4-0.4 mm and 3 nm resolution.Based on ASTM E 23-02a, Charpy Impact tests were conducted with a 300 Joules × 2 Charpy Impact machine equipped with a high-speed sampling rate data acquisition instrument (see Figure 4) in order to examine the energy absorption profile in each zone.The data acquisition instrument (manufactured by Advantech Corporation, Taipei, Taiwan) that consists of a S-type Load Cell, ADAM 3016 signal conditioner, and USB 4702-AE analog to digital converter (ADC) was set to record 45,000 samples per second.Based on ASTM E 23-02a, Charpy Impact tests were conducted with a 300 Joules × 2 Charpy Impact machine equipped with a high-speed sampling rate data acquisition instrument (see Figure 4) in order to examine the energy absorption profile in each zone.The data acquisition instrument (manufactured by Advantech Corporation, Taipei, Taiwan) that consists of a S-type Load Cell, ADAM 3016 signal conditioner, and USB 4702-AE analog to digital converter (ADC) was set to record 45,000 samples per second.Fracture surface was observed by a Hitachi SU 3500 Scanning Electron Microscope (Tokyo, Japan) and Energy Dispersive X-ray Spectroscopy, which has the ability to magnify 10-300,000× with a depth of field of 4-0.4 mm and 3 nm resolution.

Study Results
The chart presented in Figure 5 is one of the Charpy Impact test results, representing six other similar results for figures of Charpy Impact tests on seven specimens for each zone.Fracture surface was observed by a Hitachi SU 3500 Scanning Electron Microscope (Tokyo, Japan) and Energy Dispersive X-ray Spectroscopy, which has the ability to magnify 10-300,000× with a depth of field of 4-0.4 mm and 3 nm resolution.

Study Results
The chart presented in Figure 5 is one of the Charpy Impact test results, representing six other similar results for figures of Charpy Impact tests on seven specimens for each zone.The reproducibility of the test was high, considering the resemblance between the test results with Charpy Impact tests conducted with impact velocity of 3.4 m/s, which was obtained in the previous study by Janssen et al. [15].Load versus time chart as performed in Figure 5 visually shows that area under the load line, which represents the energy absorbed by the zone during impact loading, is narrower as the distance from the center of welding gets farther.The fusion zone has the ability to absorb the most energy followed by HTHAZ and two other zones, respectively.The load line of LTHAZ and Unaffected Base Metal Zone coincide with each other, which means that they are not significantly different.Total impact energy of each zone could be obtained by estimating the areas under the load line on the chart of each zone and then multiplying by 2 (2 support).Impact energy value of each zone was obtained by calculating the area under load line, and impact energy values from the indicator on the impact machine are displayed in Table 3.Some interesting findings were performed in the load versus time chart as shown in Figure 5 and in the load versus displacement chart in Figure 6a-d.The charts in all of the zones perform a negative overshoot "a", which was occurred typically in the time range of 20 to 30 ms.The reproducibility of the test was high, considering the resemblance between the test results with Charpy Impact tests conducted with impact velocity of 3.4 m/s, which was obtained in the previous study by Janssen et al. [15].Load versus time chart as performed in Figure 5 visually shows that area under the load line, which represents the energy absorbed by the zone during impact loading, is narrower as the distance from the center of welding gets farther.The fusion zone has the ability to absorb the most energy followed by HTHAZ and two other zones, respectively.The load line of LTHAZ and Unaffected Base Metal Zone coincide with each other, which means that they are not significantly different.Total impact energy of each zone could be obtained by estimating the areas under the load line on the chart of each zone and then multiplying by 2 (2 support).Impact energy value of each zone was obtained by calculating the area under load line, and impact energy values from the indicator on the impact machine are displayed in Table 3.Some interesting findings were performed in the load versus time chart as shown in Figure 5 and in the load versus displacement chart in Figure 6a-d.The charts in all of the zones perform a negative overshoot "a", which was occurred typically in the time range of 20 to 30 ms.The negative overshoot "a" indicates a plastic deformation.Previous research reported that, during plastic deformation, stainless steel 304 transformed into α' (bcc) martensite from γ (fcc) austenitic.The other study also reported the cold working process, and most of the 300 series stainless steels transform into ε (hcp) martensite and α' (bcc) martensite [16].
The presence of Cr in this alloy was suspected as a plastic deformation obstruction agent.The dislocation theory could be explained by the Cr atoms' presence dominantly in γ-Fe-Ni, they would play a role as an interstitial solute, which becomes an obstacle that hampers the motion of dislocation.Once a dislocation has stopped, an extra force was required to make the dislocation move, producing an observed upper loading in a load versus displacement graph.The presence of Cr atoms can be seen in the image by a Scanning Electron Microscope (SEM) and Energy-dispersive X-ray spectroscopy (EDS) investigation, as shown in Figure 7.The negative overshoot "a" indicates a plastic deformation.Previous research reported that, during plastic deformation, stainless steel 304 transformed into α' (bcc) martensite from γ (fcc) austenitic.The other study also reported the cold working process, and most of the 300 series stainless steels transform into ε (hcp) martensite and α' (bcc) martensite [16].
The presence of Cr in this alloy was suspected as a plastic deformation obstruction agent.The dislocation theory could be explained by the Cr atoms' presence dominantly in γ-Fe-Ni, they would play a role as an interstitial solute, which becomes an obstacle that hampers the motion of dislocation.Once a dislocation has stopped, an extra force was required to make the dislocation move, producing an observed upper loading in a load versus displacement graph.The presence of Cr atoms can be seen in the image by a Scanning Electron Microscope (SEM) and Energy-dispersive X-ray spectroscopy (EDS) investigation, as shown in Figure 7.The combination of the formation of martensite structure after plastic deformation and the presence of chromium interstisial solute, which has been described above, can be expected to be the main cause of a negative overshoot "a" occurrence.
The numbers of peak "b" variation, which was shown in the previous charts, was another interesting finding.The number of peak decreases as the increase of distance from the center of welding.The number of peaks considered has a relationship with void growth mechanism and the presence of precipitates in austenitic steel welding.Simple austenitic steels contain between 0.03% and 0.1% carbon.The solubility limit of carbon is about 0.05% at 800 °C up to 0.5 wt % at 1100 °C.The treatment at the temperature of 1050 °C to 1150 °C followed by rapid cooling would produce a solid solution saturated austenite at room temperature.This would lead to rejection of the carbon solid solution at slow cooling or reheating in the range 550-800 °C, even with the carbon content of steel being less than 0.05%.At room temperature, the structure in equilibrium condition contains austenite The combination of the formation of martensite structure after plastic deformation and the presence of chromium interstisial solute, which has been described above, can be expected to be the main cause of a negative overshoot "a" occurrence.
The numbers of peak "b" variation, which was shown in the previous charts, was another interesting finding.The number of peak decreases as the increase of distance from the center of welding.The number of peaks considered has a relationship with void growth mechanism and the presence of precipitates in austenitic steel welding.Simple austenitic steels contain between 0.03% and 0.1% carbon.The solubility limit of carbon is about 0.05% at 800 • C up to 0.5 wt % at 1100 • C. The treatment at the temperature of 1050 • C to 1150 • C followed by rapid cooling would produce a solid solution saturated austenite at room temperature.This would lead to rejection of the carbon solid solution at slow cooling or reheating in the range 550-800 • C, even with the carbon content of steel being less than 0.05%.At room temperature, the structure in equilibrium condition contains Metals 2017, 7, 543 8 of 15 austenite γ, α ferrite and carbides [17][18][19].Precipitate phase occurred at temperatures below 900 • C. When heated to 1100-1150 • C, carbide went into solution and, on cooling, a precipitate-free austenite was obtained.
When saturated austenite is heated to high temperatures, further precipitation will take place at the austenite grain boundaries.In Stainless steel welding, especially in Heat affected zones, when Stainless steel gained a heating process at more than 300 • C, the process above also takes place.The precipitation in Stainless steel welding, usually called sensitization, was observed by an optical microscope and a Scanning Electron Microscope (SEM).The presence of precipitates with dimensions of about 0.5 µm are performed in Figure 8.
When saturated austenite is heated to high temperatures, further precipitation will take place at the austenite grain boundaries.In Stainless steel welding, especially in Heat affected zones, when Stainless steel gained a heating process at more than 300 °C, the process above also takes place.The precipitation in Stainless steel welding, usually called sensitization, was observed by an optical microscope and a Scanning Electron Microscope (SEM).The presence of precipitates with dimensions of about 0.5 µm are performed in Figure 8.The sensitization process results in reduction of chromium content to the weight level of 12%, as displayed in Figure 7, with respect to the origin chromium content at the weight level of 18.4%, as shown in Table 1.This is because the segregated carbon takes up the chromium forming chromium carbides.The dimension of the chromium carbide precipitate corresponded with previous literature, which reported that the precipitate size was varying in the approximated range of 0.5-1.5 µm [20].Energy dispersive X-ray spectroscopy (EDS) was used for compositional point analysis of the precipitates.The EDS results are provided in Figure 9 and Table 4.The sensitization process results in reduction of chromium content to the weight level of 12%, as displayed in Figure 7, with respect to the origin chromium content at the weight level of 18.4%, as shown in Table 1.This is because the segregated carbon takes up the chromium forming chromium carbides.The dimension of the chromium carbide precipitate corresponded with previous literature, which reported that the precipitate size was varying in the approximated range of 0.5-1.5 µm [20].Energy dispersive X-ray spectroscopy (EDS) was used for compositional point analysis of the precipitates.The EDS results are provided in Figure 9 and Table 4.
When saturated austenite is heated to high temperatures, further precipitation will take place at the austenite grain boundaries.In Stainless steel welding, especially in Heat affected zones, when Stainless steel gained a heating process at more than 300 °C, the process above also takes place.The precipitation in Stainless steel welding, usually called sensitization, was observed by an optical microscope and a Scanning Electron Microscope (SEM).The presence of precipitates with dimensions of about 0.5 µm are performed in Figure 8.The sensitization process results in reduction of chromium content to the weight level of 12%, as displayed in Figure 7, with respect to the origin chromium content at the weight level of 18.4%, as shown in Table 1.This is because the segregated carbon takes up the chromium forming chromium carbides.The dimension of the chromium carbide precipitate corresponded with previous literature, which reported that the precipitate size was varying in the approximated range of 0.5-1.5 µm [20].Energy dispersive X-ray spectroscopy (EDS) was used for compositional point analysis of the precipitates.The EDS results are provided in Figure 9 and Table 4.The fracture resistance could not be obtained from the load versus time chart directly.It must be converted to the load versus displacement chart as seen in Figure 6.The conversion could be done by applying a series of calculation methods based on the theory of conventional dynamics [1,2].
Load versus displacement chart could then be analyzed to construct J-R curves, as shown in Figure 10, by predicting the crack length using normalization methods [2].The fracture resistance could not be obtained from the load versus time chart directly.It must be converted to the load versus displacement chart as seen in Figure 6.The conversion could be done by applying a series of calculation methods based on the theory of conventional dynamics [1,2].
Load versus displacement chart could then be analyzed to construct J-R curves, as shown in Figure 10, by predicting the crack length using normalization methods [2].The fracture resistance profiles were determined by analyzing the fracture resistance curve (Rcurve) of each zone.The R-curve in elastic-plastic materials acknowledges the fact that the resistance to fracture increases with growing crack size.The R-curve is a plot of the total energy dissipation rate as a function of the crack size.Figure 10 shows the fracture resistance curve (R-curve) of the Fusion Zone was the highest one, and then followed by HTHAZ, UBM zone and LTHAZ, respectively.The order of R-curve on Figure 10 indicates that fusion zone has the ability to absorb the most energy while LTHAZ has the ability to absorb the least one.The fact was not clearly seen on the energy versus unit of time chart in Charpy Impact test as performed in Figure 5, which made the energy absorption curve on LTHAZ coincide with the energy absorption curve in the UBM zone.The matter is probably due to insignificant precipitate content in LTHAZ.When the temperature is not enough to meet the needs of the sufficient precipitate formation, then precipitate hardening is not evoked adequately in LTHAZ.Unfortunately, the rapid loading on impact test contributes to making the differences of the energy absorption curve as a function of time between LTHAZ and UBM zone less visible.A large amount of energy that is absorbed in the impact process at a medium loading speed will be converted into various material responses such as plastic deformation, hysteresis effects, and inertia.The Charpy Impact Specimens receive high-speed loading/rapid loading on impact tests, resulting in a high strain rate.Due to the very high strain rate on the impact test, there is not enough time for the dislocation to move to a grain boundary so that no plastic deformation occurs.The material will suffer transgranular fracture.High strain rate also causes the material to have no chance The fracture resistance profiles were determined by analyzing the fracture resistance curve (R-curve) of each zone.The R-curve in elastic-plastic materials acknowledges the fact that the resistance to fracture increases with growing crack size.The R-curve is a plot of the total energy dissipation rate as a function of the crack size.Figure 10 shows the fracture resistance curve (R-curve) of the Fusion Zone was the highest one, and then followed by HTHAZ, UBM zone and LTHAZ, respectively.The order of R-curve on Figure 10 indicates that fusion zone has the ability to absorb the most energy while LTHAZ has the ability to absorb the least one.The fact was not clearly seen on the energy versus unit of time chart in Charpy Impact test as performed in Figure 5, which made the energy absorption curve on LTHAZ coincide with the energy absorption curve in the UBM zone.The matter is probably due to insignificant precipitate content in LTHAZ.When the temperature is not enough to meet the needs of the sufficient precipitate formation, then precipitate hardening is not evoked adequately in LTHAZ.Unfortunately, the rapid loading on impact test contributes to making the differences of the energy absorption curve as a function of time between LTHAZ and UBM zone less visible.A large amount of energy that is absorbed in the impact process at a medium loading speed will be converted various material responses such as plastic deformation, hysteresis effects, and inertia.The Charpy Impact Specimens receive high-speed loading/rapid loading on impact tests, resulting in a high strain rate.Due to the very high strain rate on the impact test, there is not enough time for the dislocation to move to a grain boundary so that no plastic deformation occurs.The material will suffer transgranular fracture.High strain rate also causes the material to have no chance to maintain its shape.When plastic deformation and inertia effect do not occur due to high strain rate, the material doesn't have an ability to absorb more energy before failure.J-R curve, as performed in Figure 10, displays a more obvious difference regarding the capabilities of LTHAZ and UBM zones in absorbing energy as a function of ∆a before failure.The ability of the fusion zone to absorb the most energy indicates that the zone has a better ductility then three other zones.Impact fracture macro image in Figure 11 and scanning electron microscope observation as seen in Figure 8b show ductile fracture in fusion zones clearly.The failures by ductile fracture were performed by large and deep dimple rupture.The brittle failure especially in LTHAZ was performed by a smooth surface fracture as seen in Figure 11.
Metals 2017, 7, 543 10 of 14 to maintain its shape.When plastic deformation and inertia effect do not occur due to high strain rate, the material doesn't have an ability to absorb more energy before failure.J-R curve, as performed in Figure 10, displays a more obvious difference regarding the capabilities of LTHAZ and UBM zones in absorbing energy as a function of Δa before failure.The ability of the fusion zone to absorb the most energy indicates that the zone has a better ductility then three other zones.Impact fracture macro image in Figure 11 and scanning electron microscope observation as seen in Figure 8b show ductile fracture in fusion zones clearly.The failures by ductile fracture were performed by large and deep dimple rupture.The brittle failure especially in LTHAZ was performed by a smooth surface fracture as seen in Figure 11.
the of shear stress required moving dislocations in a material is greater, causing an increase in the yield stress of the material, which also means an increase in strength of the material.The solid solution strengthening depends on a concentration of the solute atoms, modulus of the solute atoms, size of the solute atoms, valence of the solute atoms, and the symmetry of the solute field [21,22].In the present study, the critical values of fracture resistance are also related with chromium rich carbide precipitation, which was already outlined in the previous section.The energy versus unit of time chart in Figure 5 shows that the fusion zone as a zone with the highest number of peak "b" has an ability to absorb energy more than other zones.As mentioned in the previous section, the number of peaks on the graph considered have a relationship with the presence of precipitates in the zone.
In most binary systems, the second phase will be formed when the concentration of alloy is above the concentration given by the phase diagram.The alloy in the the form of the second phase in the solid solution at elevated temperatures becomes precipitate upon quenching and aging at lower temperature The precipitate has an important role in strengthening mechanism of alloy, which is called precipitation hardening [22,23].The precipitate particle acts as a barrier to dislocation in several ways.If the precipitate atoms' radii are small, the dislocations will cut through the precipitate.As a result, new surfaces get exposed to the matrix and lead the increasing of the particle-matrix interfacial energy.As the size of the second phase particle increases, it becomes increasingly difficult for the particles to cut through the material.Hence, dislocations tend to loop/to bow around the particle by Orowan Looping.At a critical diameter of about 10 nm-60 nm, dislocations will preferably cut across the obstacle, while, for a diameter more than 60 nm, the dislocations will readily loop or bow to overcome the obstacle.The precipitate with the small size (up to 0.05 µm) and intermediate size (0.05-0.5 µm) makes a contribution to strengthening the stainless steel by improving hardness and yield strength [3].When the precipitate in austenite boundaries is getting coarse, then it can easily become a void nucleation site or crack [23,24].In the present study, a few and less dominant large precipitates appeared as shown in Figure 12.
Metals 2017, 7, 543 12 of 14 called precipitation hardening [22,23].The precipitate particle acts as a barrier to dislocation in several ways.If the precipitate atoms' radii are small, the dislocations will cut through the precipitate.
As a result, new surfaces get exposed to the matrix and lead the increasing of the particle-matrix interfacial energy.As the size of the second phase particle increases, it becomes increasingly difficult for the particles to cut through the material.Hence, dislocations tend to loop/to bow around the particle by Orowan Looping.At a critical diameter of about 10 nm-60 nm, dislocations will preferably cut across the obstacle, while, for a diameter more than 60 nm, the dislocations will readily loop or bow to overcome the obstacle.The precipitate with the small size (up to 0.05 µm) and intermediate size (0.05-0.5 µm) makes a contribution to strengthening the stainless steel by improving hardness and yield strength [3].When the precipitate in austenite boundaries is getting coarse, then it can easily become a void nucleation site or crack [23,24].In the present study, a few and less dominant large precipitates appeared as shown in Figure 12.Impact fracture surface images performed in Figure 13.Void growth mechanism on the fusion zone is dominant in the stable crack extension region as indicated with very large dimples with size of about 2 µm.The dimples are less and shallower in other zones, as shown in Figure 13bd

Conclusions
The study succesfully performed the fracture resistance chart (J-R curve) of AISI 304 welding by a high speed sampling rate Charpy Impact Test.The R-curve of the Fusion Zone was the highest one, then followed by HTHAZ, the UBM zone and LTHAZ, respectively.The sequence of R curves differs from the sequence of critical fracture resistance values (JIC), and critical fracture resistance value of the Fusion Zone was highest followed by HTHAZ, LTHAZ and UBM, respectively.Compared with energy vs. unit time graph, the J-R curve chart has advantages in displaying a more obvious difference in the capabilities of the zones in absorbing energy before failure, especially between LTHAZ and UBM zones.
The present study also found the presence of Cr in all zones, which act as a plastic deformation obstruction agent, showed on the impact graph as a negative overshoot followed by increasing energy absorption.The increase of energy absorption capability, due to dislocation obstruction by the presence of a hard and strong Cr atom as a dominant particle, increases the fracture resistance profile of AISI 304.The observation throughout the impact test also showed a fine chromium carbide precipitate particle in an elevated temperature zone during the welding act as a barrier to dislocation, strengthening the AISI 304 and eventually influencing the fracture resistance profile, especially on fusion zones.

Conclusions
The study succesfully performed the fracture resistance chart (J-R curve) of AISI 304 welding by a high speed sampling rate Charpy Impact Test.The R-curve of the Fusion Zone was the highest one, then followed by HTHAZ, the UBM zone and LTHAZ, respectively.The sequence of R curves differs from the sequence of critical fracture resistance values (J IC ), and critical fracture resistance value of the Fusion Zone was highest followed by HTHAZ, LTHAZ and UBM, respectively.Compared with energy vs. unit time graph, the J-R curve chart has advantages in displaying a more obvious difference in the capabilities of the zones in absorbing energy before failure, especially between LTHAZ and UBM zones.
The present study also found the presence of Cr in all zones, which act as a plastic deformation obstruction agent, showed on the impact graph as a negative overshoot followed by increasing energy absorption.The increase of energy absorption capability, due to dislocation obstruction by the presence of a hard and strong Cr atom as a dominant particle, increases the fracture resistance profile of AISI 304.The observation throughout the impact test also showed a fine chromium carbide precipitate particle in an elevated temperature zone during the welding act as a barrier to dislocation, strengthening the AISI 304 and eventually influencing the fracture resistance profile, especially on fusion zones.

Figure 2 .
Figure 2. Microstructure of AISI 304 welding.(a) fusion zone, notch position at the center of welding; (b) high temperature heat afected zone, notch position: 4 mm from the center of welding; (c) low temperature heat affected zone, notch position: 5.5 mm from the center of welding; (d) unaffected base metal zone notch position: 7 mm from the center of welding.

Figure 2 .
Figure 2. Microstructure of AISI 304 welding.(a) fusion zone, notch position at the center of welding; (b) high temperature heat afected zone, notch position: 4 mm from the center of welding; (c) low temperature heat affected zone, notch position: 5.5 mm from the center of welding; (d) unaffected base metal zone notch position: 7 mm from the center of welding.

Figure 4 .
Figure 4. High-speed sampling rate data acquisition instrument.

Figure 4 .
Figure 4. High-speed sampling rate data acquisition instrument.

Figure 4 .
Figure 4. High-speed sampling rate data acquisition instrument.

Figure 5 .
Figure 5. Energy versus unit of time chart for Charpy Impact tests of AISI 304 welding.

Figure 5 .
Figure 5. Energy versus unit of time chart for Charpy Impact tests of AISI 304 welding.

Figure 6 .
Figure 6.Findings: negative overshoots "a" and number of peaks "b".(a) a negative overshoot "a" and lots of peak "b" in fusion zone (FZ).(b) a negative overshoot "a" and moderate number of peak "b" in high temperature heat affected zone (HTHAZ).(c) a negative overshoot "a" and moderate number of peak "b" in (LTHAZ).(d) a negative overshoot "a" and a peak "b" in unaffected Base Metal (UBM) zone.

Figure 6 .
Figure 6.Findings: negative overshoots "a" and number of peaks "b".(a) a negative overshoot "a" and lots of peak "b" in fusion zone (FZ).(b) a negative overshoot "a" and moderate number of peak "b" in high temperature heat affected zone (HTHAZ).(c) a negative overshoot "a" and moderate number of peak "b" in (LTHAZ).(d) a negative overshoot "a" and a peak "b" in unaffected Base Metal (UBM) zone.

Figure 12 .
Figure 12.The presence of less dominant large precipitate.

Figure 12 .
Figure 12.The presence of less dominant large precipitate.