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related from other country
related guideDCIs damage micromechanisms analysis is usually mainly focused on voids nucleation and growth due to the matrix-graphite nodules debonding [4-8] and numerous studies provided analytical laws to describe a single void growth, depending on the void geometries and matrix behaviour. DCI damage evolution is commonly summarized considering the following steps: - Separating between nodular graphite and matrix under low stress. - Plastic deformation in matrix around nodular graphite. - Initiation of microcracks in deformed matrix between nodular graphite. - Linkage of graphites by microcracks and formation of larger microcracks. - Linkage of main crack and selected microcracks to form macrocracks. Focusing the behaviour of a ductile iron with a completely ferritic matrix [4], no damage at graphite nodule interface was observed in the ‘‘elastic’’ part of the load- displacement curve. Few slip lines were observed emanating from the equator of the nodules, indicating a local plastic deformation of the matrix. Decohesions appeared at the pole cap of the nodules when the macroscopic yield stress was reached ( Fig. 2a). Increasing macroscopic plastic deformation induced void growth in the stress direction, thus forming ellipsoidal cavities inside which nearly undeformed nodules were embedded (Fig. 2b), failure occurred by shear instabilities linking adjacent voids. Different matrix microstructure could imply a different role played by graphite nodules. Completely pearlitic DCI [9] is characterized by the absence of irreversible damage only for very low stress values (Fig. 3a). An irreversible damage is observed already in the elastic stage (Fig. 3b): cracks could initiate and develop at the graphite nodules pole cap but also cracks initiation and propagation in pearlitic matrix is observed. Stress increase implies both cracks propagation in graphite nodules, and matrix plastic deformation and cracks propagation in pearlitic matrix. Matrix–graphite elements debonding is only rarely observed and cracks propagate inside graphite nodules. Considering austempered DCIs [10], fracture could initiate both at graphite nodules – matrix interfaces initiation and in graphite nodules (Fig. 4a); further deformation implies that microcracks inside graphite nodule propagation and connection, with a conseguent complete graphite nodule (Fig. 4b). According to Dai et alii [10], graphite nodules in austempered DCIs cannot be regarded as a voids with no strength and they do not cause micro-notch stress concentration by itself. The aim of this work was the analysis of damaging micromechanisms in a ferritic DCI. Step by step tensile tests were performed considering quasi – standard and notched specimens: their surfaces were observed by means of a scanning electron microscope (SEM) during the tensile test. Furthermore, tensile test were performed considering different deformation rates. A fully ferritic EN GJS350-22 DCI was considered (Table 1). Graphite elements were characterized by a very high nodularity, higher than 85%, with a volume fractions of about 9-10%. Investigated DCI was cut into microtensile specimens with a length x width x thickness equal to 25 x 2 x 1 mm, respectively. Specimens were ground and polished and pulled intermittently with a tensile holder and observed in situ using a -5 -1 SEM, considering at least 20 graphite elements (strain rate equal to 9.2 x 10 s ). During tensile tests, specimen deformation and applied load were measured by means of a Linear Variable Differential Transformer (LVDT) and two miniature load cell (10 kN each), respectively. Figures 5a and 5b show the tensile holder with the microtensile specimen and the tensile test machine, respectively. In order to perform a deeper investigation of damaging micromechanisms, the influence of two parameter was investigated: triaxiality and strain rate. Triaxiality influence analysis on damaging micromechanism was performed considering notched microspecimens (Fig. 6): SEM analysis was perfomed “in situ”, focusing nodules in the notch zone. Strain rate influence was investigated by means of tensile tests performed according -6 -1 to standard procedure. Two different strain rates were considered (1.3 x 10 s and -2 -1 6.7 x 10 s ) and fracture surfaces were investigated by means of a SEM. Experimental results showed that damaging micromechanism are stress level dependent. Considering tensile test results obtained on unnotched tensile microspecimens, elastic deformation stage is characterized by the absence of cracks or microvoids initiations both in matrix and in graphite elements (Fig. 7a and b, and 8a and b). Corresponding to plastic deformation stage, cracks could initiate and develop in graphite elements with an “onion-like” morphology (Fig. 7c and d) and, only corresponding to very high strain values, matrix plastic deformation becomes evident: few slip lines emanate from the equator of the nodules, thus indicating a local plastic deformation of the matrix (Fig. 7e and f). Another damaging mechanism consists in a crack initiation in the center of graphite spheroid (Fig. 8c): crack inside graphite nodule propagates with the increase of the stress value (Fig. 8d). In this case, “onion-like” mechanism is obtained only corresponding to higher stress values (Fig. 8e and f). However, no “pure” ferritic matrix–graphite elements debonding is observed. Evidences of ferritic matrix plastic deformation (slip lines) are obtained only after cracks initiation in graphite nodules. Considering Fig. 9, and focusing the graphite nodule on the right, it is evident that the very first damage consists in crack initiation in the center of grafite spheroid (Fig. 9a). The increase of the stress value implies a crack propagation in graphite element and the emanation of slip lines (Fig. 9b). Further increase of the stress value implies a propagation of an irreversible damaging of the graphite spheroid on the left (Fig. 9c), with crack that initiate from the interface graphite-matrix, corresponding to the slip lines. It is evident that experimental results shown in Figs. 7-9 do no agree with references results obtained with analogous matrix microstructure and graphite nodules morphology (e.g. [4], Fig. 2). In order to evaluate stress state on notched specimen, Von Mises stress analysis was performed considering ferritic DCI as a macroscopically homogeneous and isotropic material and using tensile test results obtained considering standard specimen as constitutive relationship. Fig. 10 shows FEM analysis results corresponding to two different nodules named “1” and “2”, with the corresponding deformation values considered for the “in situ” SEM damage analysis (named as point a, b, c and d, respectively). Nodule 1 (in the center of the notched zone) is characterized by a crack initiation and “onion-like” damage mechanism corresponding to point b (Fig. 10 and 11 b), without evident slip lines in ferritic matrix. This initiation does not correspond to a decrease of Von Mises equivalent stress, probably due to the negligeable plastic deformation of ferritic matrix. From point c (Fig. 11 c and d), slip lines are more and more evident, and matrix plastic deformation is also characterized by evident cracks that nucleate corresponding to the equator of the nodule. Fig. 11 d (almost specimen final rupture condition) is characterized by a really evident matrix deformation, with the “onion-like” damaging mechanism in the nodule that is completely developed. Nodule 2 is characterized by an increase of Von Mises equivalent stress up to a displacement of about 250 ? m (points a-c, Fig. 10). Points a – c are characterized by crack initiation and propagation in graphite nodules and by the emanation of slip lines. These slip lines are more and more evident with the increase of the deformation (Figs. 12 a – c). Point “d” in Fig 10 is characterized by a decrease of Von Mises equivalent stress: also in this case, cracks initiate in ferritic matrix (Fig. 12 d). Comparing Figs. 7 – 9 (unnotched specimen, uniaxial stress), with Figs. 11-12 (notched specimen), it is evident that ferritic matrix plastic deformation is more and more evident with the increase of triaxiality level. Furthermore, “pure” matrix-nodules debonding could not be considered as an evident damaging micromechanism. Unfortunately, it wa not possible for the authors to modify the strain rate during tensile tests “in situ” and analyze the evolution of damage level: only a “traditional” SEM fracture surfaces observation was possible. Very low strain rate value (1.3 x 10 s ) corresponds to an evident presence of cleavage and secondary cracks (Fig.13a). Focusing graphite nodules (Fig 13b), they are characterized by a modified morphology (e.g., a hole in the right side of the nodule), probably due to crack initiation and propagation inside nodules and to the activation of of the “onion-like” damaging micromechanism. Considering that “in situ” tests were -5 -1 performed using an analogous low strain rate value (9.2 10 s ), fracture surface analysis results are consistent with the results obtained with tensile tests performed “in situ”. -2 -1 Fracture surfaces obtained with a higher strain rate value (6.7 x 10 s ) do not show either cleavage or secondary cracks (Fig. 14a). Matrix microscopic ductile deformation is well developed both around graphite nodules (with an evident debonding and void growth) and with the presence of microdimples. Morphology degeneration of graphite nodules (Fig. 14b) seems to be less developed if compared with fracture surfaces obtained with lower strain rate values (Fig. 13b). This result seems to be consistent with the “pure” debonding micromechanism shown in references results (e.g. Fig. 2, [4]).Join ResearchGate to access over 30 million figures and 100+ million publications – all in one place.Copy referenceCopy captionEmbed figurePublished in
Full-text available &
Conference Paper & Sep 2009
L'incremento della deformazione plastica macroscopica comporta la crescita di vuoto nella direzione di applicazione del carico, formando in tal modo una cavità ellissoidale all'interno della quale si trovano i noduli di grafite praticamente immutati (Fig. 3b), fino ad ottenere la rottura del pezzo per coesione di vuoti adiacenti. Gli autori del presente lavoro hanno evidenziato, in attività sperimentali precedenti al presente lavoro [3] [12], come tale meccanismo non riesce ad essere rappresentativo di tutti i meccanismi di danneggiamento che effettivamente agiscono all'interno delle ghise sferoidali, ma, piuttosto, hanno mostrato come il distacco matrice-sferoide & puro & venga osservato piuttosto raramente: altri meccanismi di danneggiamento sono decisamente più frequenti, quali, ad esempio un meccanismo & a cipolla & , in cui lo sferoide vede un progressivo danneggiamento mediante una sua & esfoliazione & , e la nascita di cricche interne, spesso esattamente al centro dello sferoide (Fig. 4). L'obiettivo di questo lavoro è stato, quindi, l'approfondimento dei meccanismi di danneggiamento in una ghisa sferoidale a matrice ferritica mediante una prova di trazione effettuata utilizzando un provino di trazione con intaglio, ed osservando al SEM i differenti meccanismi di danneggiamento che vengono ad attivarsi, sia durante lo svolgimento della prova, che al termine della medesima. ABSTRACT: Le ghise sferoidali associano alle caratteristiche tipiche delle ghise (ad esempio, una elevata
colabilità), una elevata resistenza alle sollecitazioni statiche e cicliche, grazie alla particolare forma della grafite, ottenuta non attraverso lunghi e costosi trattamenti termici come nelle ghise malleabili, ma attraverso il controllo della composizione chimica. I trattamenti termici vengono effettuati quindi con l’obiettivo di controllare la microstruttura della matrice, esaltando in tal modo qualche particolare proprietà (ad esempio, resistenza a trazione, resistenza ad usura, etc.), ottenendo in tal modo ghise a matrice ferritica, perlitica, ferritoperlitica, martensitica, austenitica, etc.. Nel caso delle ghise ferritiche, il principale meccanismo di
danneggiamento identificato in letteratura è il distacco degli sferoidi dalla matrice metallica (debonding), e sono state implementate numerose numerose leggi analitiche finalizzate a descrivere la crescita dei vuoti conseguenti, considerando sostanzialmente trascurabile il ruolo svolto dalla matrice. In questo lavoro è stata effettuata una analisi sperimentale dei micromeccanismi di danneggiamento in una ghisa sferoidale utilizzando una prova di trazione su provino intagliato ed osservato al microscopio elettronico a scansione durante lo svolgimento della prova. Full-text · Article · Jan 2009 ABSTRACT: Ductile cast irons (DCIs) are characterized by an interesting combination of mechanical properties: first of all, the good castability of gray irons and the toughness of steels. This is due to the peculiar graphite elements shape, obtained by means of a chemical composition control (mainly small addition of elements like Mg, Ca or Ce). Many DCIs microstructures are available: among them, ferritic DCIs are characterized by good ductility, with tensile strength values that are equivalent to a low carbon steel. In this work, fatigue damaging micromechanisms in a ferritic DCI have been investigated by means of in–situ scanning electron microscope observations. Specimens were ground and polished and fatigue loaded by means of an electromechanic testing machine: specimens lateral surfaces were observed &in situ& using a scanning electron microscope (SEM), focusing 20 graphite nodules and considering the ferritic matrix around them. During fatigue tests, specimen deformation and applied load were measured by means of a Linear Variable Differential Transformer (LVDT) and two miniature load cell (10 kN each), respectively. On the basis of the experimental results, different fatigue damaging micromechanisms were identified, both in the graphite nodules and in the ferritic matrix. Full-text · Conference Paper · Sep 2012
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Ningbo parfect casting Co.,LTD .
Add: Room&1008 Building 666,Jin Yu& Road,Yin zhou district,Ningbo ,China
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Tel：+86-574-
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International Sales Manager :Tom Lei
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We are a China cast carbon steel company,Producing all kinds of carbon steel parts,casting process ,there are four ways，water glass casting,Silica sol casting,sand casting，lost foam casting,We are the leading China casting company. The casting parts In our China company is in good quality.Our casting parts general materials AISI 1020,AISI 1045,WCB216,Q345,20Mn5,16Mn...
We can produce cast carbon steel parts according to your requirements.Our cast carbon steel corp have different sizes of casting parts,Water glass casting dimension tolerance we could reach is CT7-8,the weight controled is about 0.2-80Silica sol casting dimension tolerance we could reach is CT 5-6，The weight controled is 0.1-60Sand casting dimension tolerance we could reach is CT11-12，the weight controled is 40-2500lost foam casting Dimension tolerance we could reach is CT8-9，The weight controled is 0.2-100kg，Parfect cast carbon steel Inc has emerged as one of the top innovators among, Our cast carbon steel parts are exported to America,Canada,England,France,Germany,Australia & South Africa Holland,Spain market...! Our casting parts are not fracture, wear-resisting, greatly reducing replacement and improve working efficiency.We have strict quality by the user consistent high praise. If you need cast carbon steel parts, please feel to contact us.
Parfect cast carbon steel Co.Ltd will provide you best price with high good quality! parfect cast carbon steel factory in China,starting since 2001, is a specialized in manufacturing all kinds of casting parts.
The reasons to choose us:1.Good Service.OEM and ODM service offered.1 year limited warranty for defective items(excluding items damaged and/or misused after receipt);2.Specialized casting Enterprise in China.Simulation of the casting system,Proficient in 3d design software,solidworks,Pro.CAD with rich experienced technical teams,Provide Complete casting S3.Quality Assurance.Well-equipped testing facilities,Good quality control petitive Prices, First Choice.Save Cost & Creating Values for You.
Process Description
Investment Casting
There are three techniques in our investment casting process including water glass technique casting, silica sol technique casting and lost foam casting.&
Water glass technique casting&
Water glass technique casting is also called cryogenic lost wax. And the dimension tolerance we could reach is CT7-8.The main material is carbon steel, alloy steel. The weight controlled is about 0.2-80 kg.&
Silica sol technique casting&
Silica sol technique casting is also called mesothermal lost wax. And the dimension tolerance we could reach is CT5-6.The main material is stainless steel ,carbon steel, alloy steel. The weight controlled is about 0.1-60kg.
Lost foam casting&
Lost foam casting is a modern form of investment casting that eliminates certain steps in the process. And the dimension tolerance we could reach is CT8-9.The main material is gray iron, dutile iron, high Cr cast iron, resistance cast iron. The weight controlled is about 0.2-100 kg.
Investment casting process
1.&Mould Designing
Strictly making 3D model based on customer's drawing dimensions, and mastered the contractibility rate for all types of material.
2. Wax Injection
Wax design of the desired castings are produced by injection molding. These designs are called patterns.
3. Assembly
The patterns are attached to a central wax stick, called a sprue, to form a casting cluster or assembly.
4. Shell Building&
The shell is built by immersing the assembly in a liquid ceramic slurry and then into
a bed of extremely fine sand. Up to eight layers may be applied in this manner.
At this point, all of the residual pattern and gating material is removed, and the ceramic mold remains. The mold is then preheated to a specific temperature and filled with molten metal, creating the metal casting
6. Mould Shell Roast:
&This process is to put the lost-wax shell into the roast furnace and make&them harder. Heating the Mould shell before casting is also to ensure&the better products surface texture.
7. Smelting the Liquid Steel:
&Allocate the chemical composition and sampling before steel casting.
8.Spectrochemistry Analysis
Inspection on materials by spectrometer testing.
9. onventional &Casting
In the conventional process, the shell is filled with molten metal by gravity pouring.
10. Cut Off&
The parts are cut away from the central sprue using a high speed friction saw.
11.Heat Treating
Carbon steel and low-alloy steel need normalizing and temper, oil-quenching, water-quenching and so on. We can set out different heat treatment method as per different requirement from customers.
12. Polishing
Polishing is to modify the out of flatness on casting head after casting&&cuttig and to modify the burring and splashings in the process of casting cycle.
13. Inspection:
Inspection of the mechanical properties, surface, internal quality, and to check if the rough dimension meet the drawing requirement for the prodcuts.
14. Machining
Cut the piece of raw material into a desired final shape and size. Now we have CNC, Lathe, milling machine, drilling machine, boring lathe and grinding machine.
15.Quality&Inspection:
Quality inspection on the machining dimension. Mainly tools we use is like specialized gauge and callipers, mircocalliper,three-dimensional and&&so on.&
16.&Storage and Delivery
&Efficiency of package goods delivery on time per your shipping requests.
&Advantage of investment casting
Wide Application Scope&
Our investment casting process is virtually unrestricted by the size ,thickness and shape complexity.
Wide Choice of Alloys&
Our investment casting process able to utilize a wide variety of alloys for common carbon steel, alloy steel, manganese steel,stainless steel ,and high-Cr & wear-resist Iron and so on.&&
Dimensional accuracy
The investment casting process is capable of producing foundry with higher accuracy than ordinary forgings and weld assembly in general condition.
Reduction of Production Costs
Investment castings are able to reduce costs in many cases such as reduced machining, less materiel waste and so on.
In addition, we own CNC machining center and CNC Lathe, so machine parts (machining parts or machinery parts),metalwork (metal products) are ok for us!}