0.1 Phason elasticity and atomic dynamics of quasicrystals 1 0.1 Phason elasticity and atom
0.1Phason elasticity and atomic dynamics of quasicrystals
F.G¨a hler,S.Hocker,U.Koschella,J.Roth,and H.-R.Trebin
Institut f¨u r Theoretische und Angewandte Physik,
Universit¨a t Stuttgart,D-70550Stuttgart,Germany
0.1.1Introduction
As the order of a quasicrystal is quasiperiodic,it can be described as an irrational cut through a periodic structure in a higher-dimensional space.This mathematical trick has important consequences for the low energy excitations that can occur.Translating the cut space to a different position is a symmetry operation,which changes the quasicrystal structure,but not its energy.A small breaking of this symmetry,by chosing a cut of small and slowly varying slope(with respect to the ideal orientation)therefore leads to low-energy Goldstone modes, called phasons.In many respects,phasons are analogous to phonons,which are small and slowly varying distortions of a structure in physical space.The distortions related to phasons rest in the complementary,internal space needed for the embedding of the quasicrystal in the higher-dimensional crystal.
In much the same way as there is an elastic energy for phonon type distortions of a solid, there is an effective elasticity theory for the phason degrees of freedom,which moreover is coupled to the phonon elasticity.A non-zero phason strain,i.e.,a non-zero slope of the cut space,will cost energy.At higher temperatures,however,phason excitations,which cor-respond to a?uctuating phason strain,will become possible.This is analogous to phonons. There is one important difference,however.Whereas phonons are usually propagating modes, phasons are believed to be diffusive.
Phason strain in a quasicrystal is connected with a rearrangement of certain local atomic con?gurations.In an elementary form these rearrangements are called phason?ips.Under-standing the dynamics of phason?ips and other atomic rearrangements of the structure of a quasicrystal is essential for the understanding of the formation and stability of quasicrystals, and also for many of their physical properties.Perfect quasicrystals are usually obtained by high temperature annealing after solidi?cation.During this process,many defects initially present are eliminated.It is therefore necessary that phason?ips,atomic diffusion,and other dynamical processes are possible and effective at these temperatures.
Atomic diffusion and phason mobility are also important for the mobility of dislocations. Unlike in a crystal,in a quasicrystal a moving dislocation leaves a phason wall in its wake. This phason wall must be smoothed out and?nally eliminated by phason?ips and diffusion processes,for otherwise the material would harden very quickly.Mobile phason?ips are therefore necessary for the ductility of quasicrystals observed at high temperatures.
There are several other interesting consequences of phason?ips.Kalugin and Katz have suggested that phason?ips provide a mechanism for atomic diffusion[1].Even though all experimental evidence indicates that vacancy mediated diffusion is dominant in quasicrystals at high temperatures[2],a phason?ip mediated diffusion mechanism cannot be ruled out at lower temperatures.Bl¨u her et al.[3]found deviations from the Arrhenius law,indicating that another diffusion mechanism becomes more ef?cient there.Due to phason-phonon coupling,
it should also be possible to excite phason?ips by applying a mechanical stress.It is conceiv-able that a periodically varying mechanical stress induces phason?ips,which likely lead to internal friction.Weller and Damson[4]have measured internal friction in quasicrystals,but it remains unclear whether the underlying atomic processes are related to phason?ips.
Our goal here is to study structure changing dynamical processes in quasicrystals by means of computer simulations.Such processes are,in particular,phason?ips and other jumps of atoms.We are not concerned with the long wavelength phonon part of the dynamics, which may be obtained by dynamical matrix methods[5,6].Our study is divided in two main parts.A?rst one is concerned with elasticity theory.Assuming a given atomic interaction,the elastic constants for phonons,phasons,and the phonon-phason coupling are determined for a simple model structure.It turns out that for simple,purely attractive pair potentials the ma-trix of elastic constants is not positive de?nite,i.e.,the model quasicrystal is only metastable for such interactions[7].A closer analysis suggests,however,how the potentials have to be modi?ed to improve the situation.With the modi?ed potentials the matrix of elastic constants becomes positive de?nite,at least at constant stoichiometry[8].Unfortunately,this does not yet imply that the quasicrystal structure is the ground state.The reason is that applying a lin-ear phason strain is not the most general deformation one can apply to a quasicrystal.Still,by Monte-Carlo simulations we?nd that the ground state of the modi?ed potentials is a supertile random tiling structure very close to the perfect quasicrystal,which is a marked improvement over the original potentials.Such an analysis is an important?rst step in selecting interaction potentials having a quasicrystalline ground state,with which one then can perform further simulations.
On a more fundamental level,dynamical processes can be studied atomistically,by using molecular dynamics simulations.This is done in a second part.There are several ways to extract information.In principle,one can compute the Van-Hove correlation function or its Fourier transform,the dynamical structure factor,which contains all information about the dy-namics.This has been attempted in[9],but it is a formidable task to do simulations providing suf?ciently good statistics.This is even so if,instead of computing the whole time-averaged Van-Hove correlation function,the computation is limited to radially averaged displacement histograms at certain time intervals[9].Often,it is therefore more promising to measure directly the quantities one is interested in.
The search for phason?ips is not easy,however.One problem is that atomic jumps and ?ips overlap with thermal vibrations,so that special?ip detectors have to be used[10].They monitor certain local con?gurations and report changes.With this method it was possible to derive jump frequencies and jump distances[10].To a certain degree it was also possible to ?gure out the correlation of the jumps of nearby atoms.But a full investigation would require additional tools or the computation of the correlation functions.
Another dif?culty is that realistic quasicrystal models require very sophisticated potentials for their stabilization.One way to avoid this problem is to use simpli?ed models which are stable with simple model potentials.From such simple models one can expect only qualita-tively correct results,but this is still interesting.With such simple models we have studied phason?ips and atomic diffusion[11],atomic jump processes[12],and even shock waves in quasicrystals[13].
Eventually,the simulation of realistic models with realistic potentials has to be mastered, however.First attempts with such potentials for decagonal Al-Cu-Co had been made in[10],
but it turned out that they were good enough only at very low temperatures.At more elevated temperatures,the Al substructure was quickly decaying,indicating that the relative energy scales of Al and transition metals is not correct.Still,it was possible to observe the expected phason?ips.In this article,we report on simulations of decagonal Al-Ni-Co with newer potentials due to Moriarty and Widom[14,15],which turn out to be much better.With these potentials,the quasicrystal is now essentially stable up to the melting point.At higher temperatures,a large part of the aluminium atoms become very mobile,so that aluminium diffusion could directly be measured.Despite this aluminium mobility,the structure remains essentially unchanged.
All the dynamical processes discussed here(phason?ips,atom jumps)are candidates for the microscopic mechanisms leading to internal friction.If mechanical stress is applied to a material,the resulting deformation need not be instantaneous,because the induced atomic rearrangements need some time to complete.In the case of a periodic external stress,with a period comparable to the relevant relaxation times,this leads to a phase shift between the ap-plied stress and the deformation,which in turn leads to dissipation.This internal friction can be observed by mechanical spectroscopy experiments[4,16].Direct simulation of internal friction,i.e.,inducing phason?ips and atom jumps by applying periodically varying mechan-ical stresses,has proved to be too ambitious for the moment,but understanding the candidate microscopic processes is an important step towards this goal.
0.1.2Phason elasticity
In this section we?rst review the general form of linear elasiticity theory for quasicrystals, and then compute all elastic constants for a simple model quasicrystal using Lennard-Jones potentials.Since not all phason elastic constants turn out to be positive[7],the potentials are then modi?ed in a systematic way in order to make the model stable against phason strains,at least at constant stoichiometry[8].The ground state structures of the modi?ed potentials are determined by Monte-Carlo simulations.They turn out to be supertile random tiling structures similar to the perfect quasicrystal.
Generalized linear elasticity theory
Elasticity theory for quasicrystals describes both phonon and phason degrees of freedom. The pure phonon part is the same as for other solids.Phonon type elastic deformations are described by the Green deformation tensor
εij=1
?ξj
+
?u j
reads
f=
1
?ξ j
.(3)
Notice that,unlike the phonon strain,the phason strain is not symmetric in its two indices. Since the two indices refer to directions in two different spaces(internal space and physical space,respectively),the phason strain must not be symmetrized.In the general case,the free elastic energy density of a quasicrystal is
f=1
2
C⊥,⊥
ijkl
χijχkl+C ,⊥
ijkl
εijχkl+O (εij,χij)3 ,(4)
where the generalized Hooke tensor now contains6+10+12=28independent elastic constants for a two-dimensional quasicrystal with a two-dimensional internal space.
In the presence of a non-trivial point symmetry,the number of independent elastic con-stants is reduced.For a two-dimensional decagonal quasicrystal,as it is considered here, the phonon strain has two symmetry invariant modes,the one-dimensional bulk deformation ε(1)and the two-dimensional shear deformationε(6)i.The phason strain splits into two two-dimensional invariant modes,χ(6)i andχ(8)i.As a consequence,a two-dimensional decagonal quasicrystal has?ve generalized elastic constants,the bulk modulusλ3/2,the shear modulus λ5/2,two phason elastic constantsλ7andλ9,and a phason-phonon coupling constantλ6. The elastic free energy density as a function of the invariant strain modes then reads f=f phonon+f phason+f coupling(5)
f phonon=1
2
λ5 ε(6)12+ε(6)22
f phason=1
2
λ9 χ(8)12+χ(8)22
f coupling=λ6 ε(6)1χ(6)1+ε(6)2χ(6)2 .
The quasicrystal model
For the atomic con?guration of our two-dimensional decagonal model quasicrystal we choose the binary tiling quasicrystal of Mikulla and Roth(Fig.1),?rst mentioned in[17].Its con-struction based on the T¨u bingen triangle tiling[18]is described in[19].This particular model has the advantage that there are unambiguous atomic con?gurations without defects for a wide range of phason strains,which is not the case for most other models.
For the atomic interactions we choose the Lennard-Jones potentials usually used for these binary tiling structures,
φij(r)=?ij σij r 6 ,(6)
where r is the distance of the two atoms and i,j are the atom types.The parameters?ij and σij are chosen such that the potential minima are at ideal nearest neighbor distances,and the minimum of the potential for different atom types is twice as deep as the other ones:?AA=?BB=1,?AB=2,σAA=1.176,σAB=1,σBB=0.6180.(7) The purpose of the deeper minimum for different atom types is to avoid phase separation.For the simulations as well as for the analytical calculations we need to cut off the potential at some?nite radius R.Furthermore,the potentials are shifted,so that they vanish at the cutoff radius R:
?φ
(r)=φij(r)?φij(R)(r -3.51898-3.51894 -3.51890 -3.5194 -3.5190 -3.5186 -0.0030.000 0.003 -3.5188 -3.5186 -3.5184 -0.003 0.000 0.003 a big atom(R=1.92).An analo- atoms.(b)Local environments (R=1.92).No.40does phason strain. system: phonon:λ3=250,λ5=90.2, phason:λ7=?2.70,λ9=0.8, coupling:λ6=?1.14.(9) Analytic computation of the phason elastic energy In the last paragraph we have seen that the phason elastic constantλ7is negative,which violates the stabilization criteria and implies that the quasicrystal is metastable at temperature zero.We therefore want to analyse how the phason elastic energy depends on the potentials, in order to learn how to modify them so that they can stabilize our model quasicrystal. For this purpose,we consider a quasicrystal with an arbitrary phason strain,but without phonon strain or local relaxation of atom positions.If we consider a cutoff radius R for the atomic interactions,the potential energy E i of a single atom depends only on the potentials φand the atomic con?guration inside the ball B R,x i with radius R around the position x i of the atom.Therefore,we can calculate the zero temperature elastic free energy by adding the potential energies of the central atoms of each local environment,multiplied by the number of occurrences N i of the environment.In the same manner we can express the total volume by the V oronoi volumes of the central atoms of the occuring environments.We can easily rewrite this in terms of the frequencies n i of the environments.These,on the other hand,are proportional to the areas of the acceptance domains A i of the environments,shown in Fig.5: f=E pot i N i V i= i n i E i i A i V i.(10) The energy E i of an atom with a given environment depends only on the potentialsφ,the corresponding acceptance domain A i depends on the phason strainχ,and the V oronoi vol-umes V i are?xed and known,so that we have derived the zero temperature free energy density r1 1.00 r3 1.54 r5 1.90 2λ7χ26+ 1 while the molecular dynamics relaxation simulations resulted in λ7=?2.70,λ9=0.8.(13) These results agree only qualitatively.One source of discrepancy is that the cutoff radius used for the simulations(R=7)was bigger than the one used for the analytic expression. However,molecular dynamics simulations with the short range potential show that the differ-ence between the two results is mainly due to atomic relaxations,which are neglected in the analytic calculations. Modi?cation of the potentials Let us now have a closer look at the analytic expressions Eq.11.The nearest neighbor interac-tion terms for the two phason elastic constantsλ7andλ9have the same weights,but opposite sign(?rst column in Eq.11).This is due to the fact,that all binary tilings with the same sto-ichiometry have the same potential energy,if only nearest neighbor interactions are assumed. For all plausible potentials the nearest neighbor part ofλ7is negative,while the one ofλ9is positive.Since the phason strain modeχ6increases the relative number of small atoms while χ8decreases it,this describes the dependence of the potential energy density on bond density. Stoichiometry preserving phason strains satisfyχ26=χ28,and thus have the phason elastic constant 1 2 1 -1 -2 00.51 1.52 Figure6:Original Lennard-Jones potentials and modi?ed potentialφAB,a mixed Lennard-Jones and Dzugutov potential. expressions phason elastic constants which are all positive,but the simulations lead to com-pletely different results.So,if the repulsive part is too strong,atomic relaxations overshadow completely the effect of the energy dependence on the frequencies of local environments,and the analytic calculation is no longer realistic. Ground states by Monte-Carlo simulations A negative phason elastic constant at temperature zero means that there exist con?gurations with lower potential energy,and thus the quasicrystal is not the ground state.For binary tiling quasicrystals with Lennard-Jones potentials a crystalline ground state was detected already by Lee et al.[23].With Monte-Carlo simulations we could essentially reproduce their results. The ground state consists of an assembly of periodic nanocrystallites.We also performed Monte-Carlo simulations with the modi?ed potentials.Here,the ground state is a supertile random tiling,with supertiles that are legal local environments from the perfect quasicrystal. However,a long range quasicrystalline order is not present,and the fat rhomb supertile seems clearly favoured(see Fig.7).Since a tiling of only fat rhomb supertiles would lead to a different stoichiometry,some supertile defects occur to adjust the ratio of the atom types.In contrast to the simulations with Lennard-Jones potentials,the perfect quasicrystal now is a low energy con?guration,even though the potential energy of the ground state as found by the Monte-Carlo simulations is clearly lower than that of the quasicrystal and its approximants. Discussion Our results show that with the original Lennard-Jones potentials the binary tiling quasicrys-tal is not stable,only metastable.For molecular dynamics simulations,this is not really a problem.Since the structure is close-packed,there are enormous energy barriers between the quasicrystal and other competing structures,which have only slightly lower energy.With Figure7:Ground state of the model quasicrystal with the modi?ed potentials. modi?ed potentials it is possible to obtain a positive phason elastic constant for stoichiom-etry preserving phason strains,whereas other phason strains can still have a negative elastic constant.In fact,thermodynamic stability does not require that stoichiometry non-preserving phason strains have positive elastic constants.Rather,for stability it is required that in an energy-composition diagram the quasicrystal is an extremal state,i.e.,it is on the boundary of the convex hull of the data points of all existing states(see[23]).An extremal state cannot decompose into two or more phases of lower energy,but the same average composition.So far,such an analysis has not been performed for the modi?ed potentials. The Monte-Carlo simulations suggest that the quasicrystal is still not the ground state,but the lowest energy states are much closer to the quasicrystal than for the Lennard-Jones poten-tials.The situation can certainly be improved by including interactions of longer range,but the effort for the analytical computations soon becomes overwhelming,because the number of different local environments grows rapidly with their size.We also note that the frequencies of all local environments considered vary quadratically with the phason strain,which implies that the elastic energy has also a quadratic form.A non-analytic elastic energy,as it is as-sumed to be necessary for an energetically stabilized quasicrystal[24],can only be obtained if the cutoff radius is larger than the matching rule radius of the tiling,which is rather big in this case[19]. The molecular dynamics simulations show that local relaxation effects are very important. Figure8:Top left:Drawing of phason?ip in decagonal Al-Cu-Co;circles are Al,squares Cu/Co.The remaining pictures show the potential landscapes of different stages of such a?ip as observed in a molecular dynamics simulation(from left to right,top to bottom).Cu/Co have deep potential minima,the?ipping Al atoms only shallow,elongated ones. They can completely overshadow the contributions from the frequencies of the(perfect)local environments.This makes an extension of the analytical computations to much larger radii doubtful.Relaxation effects also strongly modify the results from continuum elasticity theory. Atomistic considerations are therefore essential to understand the stability of quasicrystals.It is not enough to know the continuum phason elasticity. 0.1.3Atomistic simulations Molecular dynamics(MD)is an excellent tool for the study of dynamical processes at an atomistic level.In a MD simulation,the equations of motion of the particles in the system are integrated numerically over a suf?ciently long time interval.An accurate representation of the interactions between the atoms is therefore needed.Due to the aperiodic nature of qua-sicrystals,any reasonable model structure requires so many atoms,that a quantum mechanical treatment of these interactions is not feasible.For this reason,classical,effective potentials have to be used.The quality of the results of MD simulations crucially depends on the quality of these potentials,and the construction of reliable potentials is a very dif?cult task. MD simulations of decagonal Al-Cu-Co quasicrystals using realistic pair potentials have already been presented in[10],but the the potentials were able to stabilize the model structures investigated only at very low temperatures.At higher temperatures,the Al subsystem quickly melted away,while the transition metal matrix remained stable.Hence the relative energy scales of these two subsystems were probably not correct.Still,a number of interesting results could be obtained in these simulations,among them the direct observation of a phason?ip. In Fig.8,different stages of this?ip are shown,each with the potential landscape seen by the atmos involved.Cu and Co atoms are in located in deep and sharp potential minima,whereas the potential minima of the Al atoms are much shallower.Morover,the minima of the?ipping Al atoms are elongated in the direction into which the?ip takes place. In the present article,we shall concentrate on simulations carried out with new potentials derived in the framework of Moriarty’s generalized pseudopotential theory(GPT)[14,15]. These GPT potentials consist of a systematic expansion of the total energy into n-body terms, which is derived from?rst principles.For computational ef?ciency it is desirable to truncate the series as early as possible.Unfortunately,if transition metals(TM)are involved it is not always possible to terminate already after the two-body term,but Al-Lehyani et al.[25]have found that it can be done if a correction term is added to the TM-TM interactions.The correc-tion term is?tted empirically to an ab-initio calculation of a simple quasicrystal approximant [25].For computational ef?ciency,we have cut off the corrected pair potentials shortly after the third minimum,guiding the potential functions smoothly to zero.All MD simulations were carried out with the code IMD[20]developed at our institute. Using the same corrected pair potentials,Mihalkoviˇc et al.[26]have developed an opti-mized structure model of decagonal Al-Ni-Co.In Monte Carlo simulations the model was varied until a structure of minimal energy was reached.We use this model structure(with slight variations)also for our simulations.Since the model was optimized with respect to the potentials,it can be expected that they?t well together,which is important for our simulations. Stability of the model structure The structure model of Mihalkoviˇc et al.[26]essentially consists of an alternating stacking of two different layers,which are decorations of the same hexagon-boat-star(HBS)tiling.The resulting periodicity is about4?A.Like in[26],we have worked with two different decorations which differ in stoichiometry.The simpler Ni rich decoration,shown in Fig.9,has a composi-tion of Al70Ni21Co9,belonging to the the”basic Ni rich”phase[27].In the other decoration, of composition Al72Ni17Co11,some of the Ni atoms are replaced by Co(see[26]).This decoration will be termed the Co rich decoration,even though it also belongs to the Ni rich corner of the existence domain of decagonal Al-Ni-Co[27].In the follwing,we shall mainly concentrate on the Ni-rich decoration. In order to check the correctness of the energy scale,we?rst determined the melting temperature T m,by slowly heating the sample at constant pressure.The Ni rich sample melted at about1250K,whereas the Co rich sample melted at1170K.This is surprisingly close to the experimental melting temperature of the basic Ni rich phase of about1200K[27],given that the potentials were originally derived for zero temperature. Next,to check the stability of the model structures we performed simulations at constant energy,at about T=0.5T m.While both structures are essentially stable,there are a few Al atoms which change their positions during the?rst steps of the simulation.The relaxation occurs primarily inside the stars tiles:the Al atoms there move to different positions in the quasiperiodic plane,and they moreover seek alternating positions from layer to layer,breaking the4?A periodicity.The relaxed equilibrium positions are shown in Fig.9.Inside the star tile, they depend on the number of boats around the star,which in turn is determined by the type of supertile in which the star is located(Fig.9).Stars with one or three adjacent boats show an exact8?A periodicity in equilibrium,whereas stars with?ve adjacent boats show an8?A periodicity only up to about0.5T m.At higher temperatures all of the?ve equivalent positions Figure9:Ni rich decoration after relaxation.The positions of marked atoms differ from the original decoration[26].Small(large)dots indicate atoms in upper(lower)layer.Al:dark grey; Ni:black;Co:light grey.Dashed lines mark supertiles contaning the three characteristic local neighbourhoods of the star tiles.Encircled atoms occur only in every second double layer,those with solid circles in one half of the double layers,those with dashed circles in the other half. inside the star are occupied with equal probability,and the periodicity is completely broken locally.At very high temperatures,the decoration of the hexagon supertile is further modi?ed and becomes completely symmetric.For the following simulations,we have directly used the modi?ed decoration corresponding the real equilibrium structure.The same modi?cations to the original model of Mihalkoviˇc et al.[26]have also been observed in[28]. Aluminium diffusion At temperatures above0.6T m,signi?cant Al diffusion is observed(Fig.10).Only Al atoms neighboring Co atoms are involved in the diffusion,but these form a sizeable fraction of all Al atoms.Positions with mobile Al atoms are suf?ciently close to each other that long range diffusion is possible.Other Al positions can remain very stable even at high temperature, particularly those in rings with?ve Al and?ve Ni atoms.The stability of these rings can also be seen in(time averaged)atom density maps(Fig.11),where such Al positions are very sharp,whereas those near Co atoms are completely smeared out. As noted earlier,at temperatures close to T m the decoration of the supertile hexagon(a boat-star pair)becomes symmetric.In the atom density maps of these supertile hexagons,one can see smeared-out parts of the Al distribution,namely pairs of banana-shaped regions near each of the Co atoms(Fig.11),and continuous,zig-zag shaped distributions along the z-axis (Fig.12),arising from the central dot in the supertile hexagon.These and other smeard-out parts of the Al distribution open diffusion channels.They are suf?ciently close to each other Figure10:Al motion at T=0.9T m.Dark grey,large:Ni;light grey,large:Co;dark grey, small:Al initial positions;light grey,small:Al positions after1ns.Initial and?nal Al positions are connected. Figure11:Atom density map,projected on xy plane.Co positions are marked with circles;Ni positions appear as sharp,almost black dots,whereas Al positions are grayish. that long-range Al diffusion is possible.Continuous channels in the atom density maps have also been observed by Henley et al.[28].Fig.12suggests that a number of aluminium atoms leave the layers,and spend considerable time between the layers.This kind of disorder could explain part of the diffuse diffraction intensity observed in x-ray scattering at high tempera-tures[29]. Due to the high Al diffusivities,it has been possible to measure the Al diffusion constant Figure 12:Atom density map similar to Fig.11.Here,the same slab of material is shown in projections on the xy-and the xz-plane.The central dot in a supertile hexagon consists of a continuous density along a zig-zag in the z-direction,which provides a diffusion channel.05 10152025024681012 14161820 m e a n s q u a r e d i s p l a c e m e n t [?2]time [ns]T=1010K T=1044K T=1079K T=1114K T=1148K T=1183K T=1218K T=1253K 010 20 30 40 50 60 70 0246810 1214161820 m e a n s q u a r e d i s p l a c e m e n t [?2]time [ns]T=1010K T=1044K T=1079K T=1114K T=1148K T=1183K T=1218K T=1253K Figure 13:Mean quare displacement of Al as a function of time,for different temperatures.Shown are the displacements in the x-direction (top)and the z-direction (bottom). as a function of temperature and pressure.As expected,it follows the usual Arrhenius law: D =D 0e ? ?H +p ?V 1e?131e?12 1e?110.80.91 1.1 1.2 1.3 1.4 1.5 1.6D [m 2/s ]1000/T [1/K]z Co?rich x Co?rich z Ni?rich x Ni?rich 1e?12 1e?11 1e?10 0510152025303540D [m 2s ?1]pressure [MPa] z?direction y?direction x?direction Figure 14:Left:Arrhenius plot for Al diffusion for the Ni rich and the Co rich decoration.Right:Pressure dependence of diffusion constant. At ?rst we chose the volume of the system corresponding to a pressure p =0,and made a series of simulations with varying temperature.The resulting mean square displacements are shown in Fig.13.From these curves (and similar ones for the Co rich decoration)the activation enthalpies H and preexponential factors D 0could be determined,separately for the x-,the y-,and the z-direction.The resulting Arrhenius plot (Fig.14,left)shows that the activation enthalpies are almost isotropic in the Co rich case,but somewhat anisotropic in the Ni rich case,and that both the activation enthalpies and the preexponential factors for the Ni rich composition exceed the values for the Co rich composition.Furthermore,the diffusion is isotropic in the xy-plane,as it is imposed by decagonal symmetry.The numerical values are given in Table 2. Table 2:Activation enthalpies and pre-exponential factors for two decorations. Decoration Co rich 0.89 0.64 1.8×10?8 6.3×10?9 high temperatures.A sizable fraction of the Al atoms,namely those near Co atoms,become very mobile at high temperature,which leads to a high Al diffusivity,comparable to that of vacancy diffusion in fcc Al[30].The diffusion we observe cannot be vacancy mediated,how-ever.The activation volume we determined is too small for vacancy diffusion[31].Moreover, there are no vacancies present in the structure,and during the short simulation time vacancies cannot form.Our results do not exclude,however,that there is also vacancy diffusion,once vacancies are present.Mehrer and Galler[31]have found that in decagonal Al-Ni-Co the diffusion of many transition metals,but also that of Zn,is predominantly vacancy mediated, as it is the case for other quasicrystals.The diffusion mechanism we observe must be due to the particular(local)structure of the quasicrystal. 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[31]H.Mehrer and R.Galler,Vacancy-mediated diffusion in quasicrystalline alloys,J.Al- loys Compd.342(2002)296. 简单的四则运算计算器程序 注：1、报告内的项目或内容设置，可根据实际情况加以调整和补充。 2、教师批改学生实验报告时间应在学生提交实验报告时间后10日内。 附件：程序源代码 // sizheyunsuan.cpp : Defines the entry point for the console application. #include 兰坪县金顶镇文兴农贸市场建设项目《降水工程》专项施工方案 编制人：黄正勇 审核人：罗国强 审批人：张克林 云南瑞石建筑工程有限公司 2019年3月17日 目录 一、工程概况 (1) 二、工程地质 (4) 三、施工工艺 (4) 四、机械设备 (8) 五、质量控制 (8) 六、安全生产、文明施工措施 (8) 一、工程概况 本工程工程名称为兰坪县金顶镇文兴农贸市场建设项目工程，工程位于兰坪县金顶镇文兴社区环城小区。 一、土建概况 (一）兰坪县金顶镇文兴农贸市场建设项目--1栋综合楼工程： 1、建筑面积:403.99m2； 2、地上共2层，无地下室建筑总高7.05米； 3、建筑物室内地面标高±0.000=2288.440； 4、结构形式：砖混结构； 5、基础形式采用柱下条形基础。 兰坪县金顶镇文兴农贸市场建设项目--1栋综合楼工程建筑结构安全及设计使用年限： 1. 建筑结构安全等级：一级； 2. 结构设计使用年限： 50年； 3. 建筑抗震设防类别：乙类设防； 4. 地基基础设计等级：乙级； 5 .结构抗震等级：砖混一级，结构抗震构造措施：按7度一级。建筑场地类别：Ⅱ类。 (二）兰坪县金顶镇文兴农贸市场建设项目--2栋综合楼工程： 1、建筑面积:358.23m2； 2、地上共2层，无地下室建筑总高7.05米； 3、建筑物室内地面标高±0.000=2289.000； 4、结构形式：砖混结构； 5、基础形式采用柱下条形基础。 兰坪县金顶镇文兴农贸市场建设项目--2栋综合楼工程建筑结构安全及设计使用年限： 1. 建筑结构安全等级：一级； 2. 结构设计使用年限： 50年； 3. 建筑抗震设防类别：乙类设防； 4. 地基基础设计等级：乙级； 计算器使用说明书目录 取下和装上计算器保护壳 (1) 安全注意事项 (2) 使用注意事项 (3) 双行显示屏 (7) 使用前的准备 (7) k模式 (7) k输入限度 (8) k输入时的错误订正 (9) k重现功能 (9) k错误指示器 (9) k多语句 (10) k指数显示格式 (10) k小数点及分隔符 (11) k计算器的初始化 (11) 基本计算 (12) k算术运算 (12) k分数计算 (12) k百分比计算 (14) k度分秒计算 (15) kMODEIX, SCI, RND (15) 记忆器计算 (16) k答案记忆器 (16) k连续计算 (17) k独立记忆器 (17) k变量 (18) 科学函数计算 (18) k三角函数／反三角函数 (18) Ch。6 k双曲线函数／反双曲线函数 (19) k常用及自然对数／反对数 (19) k平方根﹑立方根﹑根﹑平方﹑立方﹑倒数﹑阶乘﹑ 随机数﹑圆周率（π）及排列／组合 (20) k角度单位转换 (21) k坐标变换（Pol（x, y）﹐Rec（r, θ）） (21) k工程符号计算 (22) 方程式计算 (22) k二次及三次方程式 (22) k联立方程式 (25) 统计计算 (27) 标准偏差 (27) 回归计算 (29) 技术数据 (33) k当遇到问题时 (33) k错误讯息 (33) k运算的顺序 (35) k堆栈 (36) k输入范围 (37) 电源（仅限MODEx。95MS） (39) 规格（仅限MODEx。95MS） (40) 取下和装上计算器保护壳 ?在开始之前 (1) 如图所示握住保护壳并将机体从保护壳抽出。 ?结束后 (2) 如图所示握住保护壳并将机体从保护壳抽出。 ?机体上键盘的一端必须先推入保护壳。切勿将显示屏的一端先推入保护壳。 使用注意事项 ?在首次使用本计算器前务请按5 键。 ?即使操作正常﹐MODEx。115MS/MODEx。570MS/MODEx。991MS 型计算器也必须至少每3 年更换一次电池。而MODEx。95MS/MODEx。100MS型计算器则须每2 年更换一次电池。电量耗尽的电池会泄漏液体﹐使计算器造成损坏及出现故障。因此切勿将电量耗尽的电池留放在计算器内。 ?本机所附带的电池在出厂后的搬运﹑保管过程中会有轻微的电源消耗。因此﹐其寿命可能会比正常的电池寿命要短。 ?如果电池的电力过低﹐记忆器的内容将会发生错误或完全消失。因此﹐对于所有重要的数据﹐请务必另作记录。 ?避免在温度极端的环境中使用及保管计算器。低温会使显示画面的反应变得缓慢迟钝或完全无法显示﹐同时亦会缩短电池的使用寿命。此外﹐应避免让计算器受到太阳的直接照射﹐亦不要将其放置在诸如窗边﹐取暖器的附近等任何会产生高温的地方。高温会使本机机壳褪色或变形及会损坏内部电路。 ?避免在湿度高及多灰尘的地方使用及存放本机。注意切勿将计算器放置在容易触水受潮的地方或高湿度及多灰尘的环境中。因如此会损坏本机的内部电路。 双行显示屏 高都 1 井等 3 个井站泡沫排水采气工 艺 大修工程 施工组织设计 编制人: 审核人： 批准人： 江苏省工业设备安装集团有限公司 年月日 目录 第一章编制依据. (1) 1.1 遵循的规范和标准 (1) 1.2 编制原则 (1) 第二章工程概况. (1) 2.1 工程名称 (1) 2.2 工程地点 (2) 2.3 建设工期 (2) 2.4 工程概要 (2) 第三章施工部署. (6) 3.1 施工准备 (7) 3.2 施工机具、设备进场计划 (7) 3.3 施工部署 (7) 3.4 临时物资中转场的布置 (8) 3.5 施工组织机构 (8) 3.6 施工人员及设备材料配备表 (9) 第四章主要施工技术方案. (9) 4.1 土建部分 (9) 4.2 管道敷设及特殊地段处理 (11) 第五章质量保证措施. (13) 5.1 质量方案 (13) 5.2 质量目标和质量管理 (14) 5.3 质量控制机构 (14) 5.4 质量责任 (15) 5.5 质量控制要素 (17) 5.6 质量检测及控制程序 (23) 5.7 质量监督与检查 (24) 第六章HSE 管理措施 (25) 6.1HSE 管理体系与组织机构 (25) 6.2 岗位HSE职责 (26) 第七章其它保障措施. (29) 7.1 配合作业 (29) 7.2 设备、材料接、保、检、运措施 (29) 7.3 施工场地治安保卫管理计划 (30) 7.4 施工环保措施计划 (31) 7.5 成品保护和工程保修工作的管理措施和承诺 (32) 7.6 与发包人、监理及设计人的配合 (33) 第八章工程竣工资料及工程总结. (34) 8.1 竣工资料 (34) 8.2 工程总结 (34) 附表一：拟投入的主要施工机械设备表. (35) 附表二：拟配备本工程的试验和检测仪器设备表. (36) 附表三：劳动力计划表. (37) 附表四：计划开、竣工日期和施工进度网络图. (38) 保存计算过程的计算器 Java程序设计课程设计报告保存计算过程的计算器 目录 1 概述.............................................. 错误！未定义书签。 1.1 课程设计目的............................... 错误！未定义书签。 1.2 课程设计内容............................... 错误！未定义书签。 2 系统需求分析.......................................... 错误！未定义书签。 2.1 系统目标................................... 错误！未定义书签。 2.2 主体功能................................... 错误！未定义书签。 2.3 开发环境................................... 错误！未定义书签。 3 系统概要设计.......................................... 错误！未定义书签。 3.1 系统的功能模块划分......................... 错误！未定义书签。 3.2 系统流程图................................. 错误！未定义书签。4系统详细设计........................................... 错误！未定义书签。 5 测试.................................................. 错误！未定义书签。 5.1 测试方案................................... 错误！未定义书签。 5.2 测试结果................................... 错误！未定义书签。 6 小结.................................................. 错误！未定义书签。参考文献................................................ 错误！未定义书签。附录................................................ 错误！未定义书签。 附录1 源程序清单...................................... 错误！未定义书签。 井点降水专项施工方案 工程名称＿如皋市红星市场扩建改造及商住楼工程 编制＿＿＿＿＿＿＿＿＿＿＿＿＿＿ 审核＿＿＿＿＿＿＿＿＿＿＿＿＿＿ 批准＿＿＿＿＿＿＿＿＿＿＿＿＿＿ 日期＿＿＿＿＿＿＿＿＿＿＿＿＿＿浙江广丰建设有限公司 目录 一、工程概况 (3) 二、施工准备 (3) 三、施工工艺 (4) 四、注意事项 (5) 五、轻型井点降水系统拆除 (6) 六、质量验收标准 (6) 七、环境安全措施 (6) 轻型井点降水施工方案 一.工程概况: 如皋市红星市场扩建改造及商住楼开发工程位于如皋市如城镇红星村，中山西路北侧，总建筑面积43146平方米，其中住宅15860平方米，农贸市场5139平方米，超级市场8498平方米，商务酒店1156平方米。 该工程包括一幢9层综合楼和4幢住宅楼（两幢6层商住楼和两幢5层住宅楼）。 综合楼平面总尺寸为95.5mX75.4m，主体结构高度38.1m，机房高度41.1m。其中主楼地上9层。一二层商铺，超级市场层高5米及6米，三层及三层以上商务酒店层高3.5米；八层层高3.9米，九层层高4.9米。 商住楼包括1#、2#、3#、4#、四个单体。１#楼平面尺寸为43.6mX10.9m，高18.38m，屋面最高19.95m。地上一层车库+五层住宅+阁楼，其中底层车库层高2.19m，住宅部分层高为2.8m。2#楼平面尺寸为51.46mX14.8m，高19.79m，屋面最高21.36m。地上一层商铺+五层住宅+阁楼，其中底层商铺层高3.6m，住宅部分层高为2.8m。3#楼平面尺寸为65.4mX10.9m，高18.38m，屋面最高19.95m。地上一层车库+五层住宅+阁楼，其中底层车库层高2.19m，住宅部分层高为2.8m。4#楼平面尺寸为55.3mX14.8m，高19.78m，屋面最高21.36m。地上一层商铺+五层住宅+阁楼，其中底层商铺层高3.6m，住宅部分层高为2.8m。 本工程场地基本平整，+0.000为黄海高程5.65米，本基坑开挖在3.05米左右，根据本工程的勘测报告显示，初见水位标高为2.57—3.11M，稳定水位标高为2.67—3.21M 为确保施工安全，达到经济、安全的目的，本工程采用轻型井点降水施工。 二.施工准备 （一）施工机具 1.管：φ45，壁厚为3.0mm的无缝钢管或镀锌管，长5.0m左右，一端用厚为4.0mm的钢板焊死，在此端1m长范围内，在管壁上钻φ15mm的小圆孔，孔距为25mm，外包两层滤网，滤网采用编织布，外部再包一层网眼较大的尼龙丝网，每隔50～60mm用10号铅丝绑扎一道，滤管另一端与井点管进行连接。 2.井点管：φ45，壁厚为 3.0mm的无缝钢管或镀锌管。 3.连接管：透明管或胶皮管，与井点管和总管连接，采用8号铅丝绑扎，应扎紧以防漏气。 5.抽水设备：根据设计配备离心泵、真空泵或射流泵，以及机组配件和水箱。 6.移动机具：自制移动式井架(采用旧设备振冲机架)、牵引力为6t的绞车。 7.水枪：φ50×5无缝钢管，下端焊接一个φ16的枪头喷嘴，上端弯成大约直角，且伸出 冲击管外，与高压胶管连接。 8.蛇形高压胶管：压力应达到1.50MPa以上。 9.高压水泵：100TSW-7高压离心泵，配备一个压力表，作下井管之用。 （二）材料 粗砂与豆石，不得采用中砂，严禁使用细砂，以防堵塞滤管网眼。 vmware部署实施手册 目录............................................................................................................................................. ESXI 1.ESXi 4 安装............................................................................................................................. . 系统安装以及设置.............................................................................................................. 2.vShpere Client安装................................................................................................................ . vSphere Client 安装........................................................................................................ .虚拟机管理............................................................................................................................ 3．平台管理 . 平台查看以及功能..................................................................................................................................... . 新建虚拟机.编辑虚拟机设置..................................................................................................................... . VMware Tool 安装...................................................................................................................................... . 虚拟机克隆................................................................................................................................................. ．虚拟机模板制作......................................................................................................................................... . 从虚拟机模板部署新的虚拟机................................................................................................................. . 虚拟机迁移................................................................................................................................................. 域控 装条件 在运行中输入“Dcpromo”进行安装 用户帐号的添加和管理 文件重定向策略 NAS存储 登录NAS系统 网络设置 安全 服务 共享 备份 现况 ESXI安装 4 安装 通过 DVD 引导文本安装模式简介 . 系统安装以及设置 接下来将ESXi 安装光盘放在光驱并开启服务器。服务器从光盘启动后将出现如下 界面，选择下图中的“ESXi Installer”进入安装过程。 目录 1.基本功能描述 (1) 2.设计思路 (1) 3.软件设计 (10) 3.1设计步骤 (10) 3.2界面设计 (10) 3.3关键功能实现 (12) 4.结论与心得 (14) 5.思考题 (15) 6.附录 (17) 6.1调试报告 (17) 6.2测试结果 (18) 6.3关键代码 (21) 实用计算器程序 1.基本功能描述 （1）可以计算基本的运算：加法、减法、乘法、除法。 （2）可以进行任意加减乘除混合运算。 （3）可以进行带任意括号的任意混合运算。 （4）可以进行单目科学运算：1/x、+/-、sqrt、x^2、e^2等。 （5）可以对显示进行退格或清除操作。 （6）可以对计算结果自动进行存储，并在用户需要的时候查看，并且可在其基础上进行再运算操作。 （7）界面为科学型和普通型，可在两界面间通过按钮转换。 2.设计思路 计算器属于桌面小程序，适合使用基于对话框的MFC应用程序设计实现。首先要思考的问题是：我的程序需要实现什么样的功能？需要哪些控件？需要哪些变量？需要哪些响应？ 我们知道基于对话框的MFC应用程序的执行过程是：初始化、显示对话框，然后就开始跑消息循环列表，当我们在消息循环列表中获取到一个消息后，由相应的消息响应函数执行相应的操作。根据这个流程我们制定出计算器程序的程序框架主流程图，如下页图1所示。 根据程序主流程图可以看出，我们需要一些能响应用户操作的响应函数来实现我们的计算器相应按键的功能。 图1 程序主流程图 说明：所以流程图由深圳市亿图软件有限公司的流程图绘制软件（试用版）绘制，转 存PDF后导出为图片加入到word中的，所以可能会打印效果不好，但确实为本人绘制。 高空作业施工方案 沈阳华生建设工程有限公司 黎明生活坊项目 2012年4月1日 目录 第一章编制依据 (1) 第二章工程概况 (1) 第三章高空作业的函意 (1) 第四章建筑工程高空作业坠落事故多发的原因 (1) 第五章高空作业施工方案 (3) 一、领导重视、落实责任 (3) 二、严把技术措施关 (3) 第六章高空坠落事故预防 (10) 一、控制人的因素 (10) 二、控制手的因素 (10) 三、控制操作方法因素 (11) 四、控制组织管理因素 (11) 五、控制环境因素 (11) 第七章高空作业安全防护设施验收 (11) 第一章编制依据 1、《建筑工程预防高处坠落事故若干规定》（建质[2003]82号） 2、《建筑施工安全检查标准》（JGJ 59—99） 3、《建筑施工高处作业安全技术规范》（JGJ 80—91） 4、《钢管扣件式脚手架安全技术规范》（JGJ 130—2001） 5、施工组织设计 6、施工图纸 第二章工程概况 属于框剪结构；地上16层；地下1层，标准层层高：2.9m。 施工单位：沈阳华生建设工程有限公司 工程名称：黎明生活坊 地理位置：大东区和睦南一路 建设单位：辽宁宝兴房地产开发有限公司 主要功能及用途：住宅 第三章高空作业的涵义 一、所谓高处作业是指人在一定位置为基准的高处作业。国家标准规定：凡在坠落高度基准面2米以上(含2米)有可能坠落的高处进行作业，都称为高处作业。根据这规定，在建筑施工过程中涉及到高处作业的范围，是相当广泛的。 二、为便于操作过程中做好安全防范工作，有效地防止人与物从高处坠落的事故，根据建筑行业的特点，在建筑安装工程施工中，对建筑物和构筑物结构范围以内的各种形式的洞口、临边作业、悬空与攀登作业，操作平台与立体交叉作业，以及在结构主体以外的场地和通道旁的各类洞、坑、沟、槽等工程的施工作业，只要符合上述条件的场地作为高处作业，并加以防护。 Vmware虚拟化完整配置VSPHERE 6.7虚拟化搭建及配置 kenny 目录 一、安装环境介绍 (3) 二、安装与配置vmware vsphere 6.7 (4) 1、安装vsphere 6.7 (4) 2、配置密码 (4) 3、配置DNS、主机名和IP地址 (5) 三、配置Starwind V8 (7) 四、安装vcenter server 6.7 (10) 1、安装vcenter server(自带嵌入式数据库) (10) 2、配置外部数据库SQL SERVER 2008 (15) 3、使用外部数据库安装Vcenter server (19) 五、创建数据中心和群集HA (24) 1、新建数据中心 (24) 2、创建群集HA (24) 六、添加ESXI主机和配置存储、网络 (26) 1、添加ESXI主机到群集中 (26) 2、配置存储 (28) 3、添加网络 (30) 七、创建虚拟机 (32) 1、上传镜像至共享存储 (32) 2、新建虚拟机 (33) 3、将虚拟机克隆为模板 (37) 4、通过模板部署新虚拟机 (39) 八、物理机迁移至ESXI（P2V） (44) 1、迁移windows物理机 (44) 2、迁移Linux物理机 (49) 九、vmotion迁移测试 (51) 十、HA高可用测试 (53) 十一、VMware vSphere FT双机热备 (54) 十二、vSphere Data Protection配置部署 (57) 1、部署VDP模板 (57) 2、配置VDP (62) 3、创建备份作业 (68) 十三、附录 (72) 高速公路集水井施 工方案 高速公路集水井施工方案 一、工程概况 本项目为阜新到朝阳高速公路建设项目，路面共分8个合同段，本标段为第3合同段。设计桩号范围为K324+500～ K362+139.052，本合同有断链一处，K356+151.624=K356+000，链长151.624米，路线全长37790.676米。本标段有互通立交一处，为北票立交；服务区一处，为北票服务区。路面从下到上的结构层为：15cm（12cm）砂砾垫层+21cm(16cm)水泥稳定砂砾掺碎石底基层+21cm(16cm)水泥稳定碎石基层+7cm LAC-25I粗粒式沥青混凝土下面层+6 cm LAC-20I中粒式沥青混凝土中面层+4cm SMA-13L 沥青玛蹄脂碎石表面层。合同工期为：14.5个月。 基层施工已经完毕，已经具备集水井施工的条件；为不影响面层的施工；特申请集水井分项工程开工。 二、施工准备情况 全线水准点和导线点复测审批工作已完成，满足施工测量的需要；集水井施工涉及的C15﹑C30混凝土等配合比工作已完成，具备施工的前提条件。 三、施工流程与施工工艺 （一）施工流程 1﹑大集水井施工流程 施工放样→开挖沟槽→铺筑砂砾垫层→C15垫层混凝土浇注→支模→井身浇注→拆模→养护→盖板安装 2、小集水井施工流程 施工放样→预制→开挖沟槽→C15垫层混凝土浇注→小集水井安装→盖板安装 （二）施工工艺 1、大集水井施工 （1）、测量放线 在施工前根据已放出的中线确定大集水井位置，用白灰撒出大集水井的边线。 （2）、开挖沟槽 根据撒出的白灰线，开挖宽71cm、长140cm、垫层底面以下深122cm的沟槽，槽壁要直立。 （3）、铺筑砂砾垫层 在大集水井底部铺筑30cm的砂砾垫层，砂砾要干净无杂物，砂砾垫层要夯实。 （4）、C15垫层混凝土浇注 在砂砾垫层上铺筑10cm的C15混凝土垫层。混凝土要振捣密实。 （5）、支模 模板宜优先选用钢模，模板要涂抹废机油或肥皂水防止粘模，模板支立要有足够的强度和刚度，防止出现涨模等现象；而且模板之间要接缝要严密不漏浆。 （6）、井身浇注 Vmware 虚拟化完整配置VSPHERE 6.7虚拟化搭建及配置 kenny 目录 一、安装环境介绍 (3) 二、安装与配置vmware vsphere 6.7 (4) 1、安装 vsphere 6.7 (4) 2、配置密码 (4) 3、配置 DNS、主机名和 IP 地址 (5) 三、配置 Starwind V8 (6) 四、安装 vcenter server 6.7 (9) 1、安装 vcenter server( 自带嵌入式数据库) (9) 2、配置外部数据库SQL SERVER 2008 (14) 3、使用外部数据库安装Vcenter server (17) 五、创建数据中心和群集HA (21) 1、新建数据中心 (21) 2、创建群集 HA (21) 六、添加 ESXI主机和配置存储、网络 (23) 1、添加 ESXI主机到群集中 (23) 2、配置存储 (24) 3、添加网络 (26) 七、创建虚拟机 (28) 1、上传镜像至共享存储 (28) 2、新建虚拟机 (29) 3、将虚拟机克隆为模板 (33) 4、通过模板部署新虚拟机 (35) 八、物理机迁移至ESXI（ P2V） (40) 1、迁移 windows 物理机 (40) 2、迁移 Linux 物理机 (45) 九、 vmotion 迁移测试 (47) 十、 HA 高可用测试 (49) 十一、 VMware vSphere FT 双机热备 (50) 十二、 vSphere Data Protection 配置部署 (52) 1、部署 VDP模板 (52) 2、配置 VDP (57) 3、创建备份作业 (63) 十三、附录 (68) 高位井施工方案 1、工程概况 略 2、工程测量 定位程序：资料审核→内业核算→外业校测→定位测放→定位自检→定位验线。 2.1测量定位 本工程施工场地小，施工受现场条件影响较大，测量定位较为繁复。测量定位采用先进的高精度红外测距仪、全站仪、经纬仪及水平仪，根据提供的红线界桩点和有关图纸，确定各个轴线控制点，组成轴网控制，并将控制点延伸至施工影响范围以外的区域上，且采取混凝土加固保护措施，定位工作由我公司专职测量师完成。 2.2轴线、标高控制 根据地面层设置的控制网、控制点逐层向下传递。测量设备为经纬仪和钢尺，具体方法为：利用经纬仪通过基坑外的控制点来形成控制轴线，用经纬仪钢尺校对，调整误差，最后细分全部轴线；标高的控制采用钢尺从上层引入标高，基点位置固定，通过出入预留口引至下层，同样应调整钢尺的温度及拉力误差，然后利用水准仪同层抄平。 2.3测量精度的控制及误差范围 测角：采用三测回，测角过程中误差控制在2"以内，总误差5mm以内； 测弧：采用偏角法，测弧度误差控制在2"以内； 测距：采用往返测法，取平均值； 量距：用鉴定过的钢尺进行量测并进行温度修正； 每层轴线之间的偏差控制在在5mm以内，层高垂直偏差在5mm以内。 2.4沉降观测计划 （1）根据本工程结构形式的特点，先按照业主提供的高程基准点，将其引测至施工地块内，设置若干控制点，将其固定在基地内不易被破坏的部位，安排专人进行保护，在埋设点保持稳定后测定控制点的高程，并记录其数据，作为以后工程测量基准点，且由专业测量人员定期对其复测，与外界高程基准点进行校核； （2）根据本工程施工范围广、沉井下沉深度深等特点，在建筑物设置施工期间暂时沉降观测点和永久沉降观测点两种。施工期间暂时沉降观测点采用钢筋直接与主筋电焊连接分别固定于结构底板和侧墙内侧。永久沉降观测点设置采用铜质沉降标记预埋件，预埋于结构侧墙内； （3）沉降观测采用测量精度Ⅱ级水准测量，底板浇捣完毕后测得初读数，以后每施工一层测读一次。即每施工一层应进行一次沉降观测。工程竣工后，第一年测沉4次； （4）沉降观测应做好详细记录，认真整理沉降资料，汇入工程验收技术档案。 3、高位井（兼作顶管工作井）沉井施工 本工程高位井采用矩形沉井，尺寸为24.4m×11.0m×22.1m，井内有纵横隔墙将高位井分为一个进水室和两个出水室及一个应急排放管出水室。进水室与排海泵站的出水箱涵相衔接，两个出水室和一个应急排放管出水室分别与深海排放管和应急排放管相衔接。 3.1施工准备 施工前在沉井施工地点进行钻孔了解场地内详细地质情况，查清和排除地面及地面下3m内的障碍物。 3.2基坑开挖 （1）为了减少沉井下沉时的挖土工作量，沉井砼结构制作前在沉井位置开挖基坑。根据现场的施工条件，基坑开挖尺寸为28.4m×15.0m，即离沉井的外 内蒙古伊泰广联煤化有限责任公司红庆河煤矿副井井塔及锁口工程 施 工 组 织 设 计 中煤第五建设有限公司 2015年1月 1.编制依据 1.1*******煤矿副井井塔及锁口工程招标文件及有关施工图纸等资料。 编号：YTZB2014-145 1.2 现行国家规范标准： 1.2.1 《工程测量规范》GB50026-2007； 1.2.2 《建筑地基基础工程施工质量验收规范》GB50202-2009； 1.2.3 《砌体工程施工质量验收规范》GB50203-2002； 1.2.4 《混凝土工程施工质量验收规范》GB50204-2002（2011版）； 1.2.6 《混凝土泵送技术规程》JGJ10-2011； 1.2.7 《钢筋焊接及验收规程》JGJ18-2003； 1.2.8 《屋面工程施工质量验收规范》GB50207-2012； 1.2.9 《建筑地面工程施工质量验收规范》GB50209-2002； 1.2.10 《建筑装饰装修工程施工质量验收规范》GB50210-2001； 1.2.11 《建筑给水排水及采暖工程施工质量验收规范》GB50242-2002； 1.2.12 《建筑电气工程施工质量验收规范》GB50303-2012； 1.2.13 《建筑工程施工质量验收统一标准》GB50300-2013； 1.2.14 《建筑施工安全检查标准》JGJ59-2011； 1.2.15 《建筑施工高处作业安全技术规范》JGJ80-2011； 1.2.16 《高层建筑混凝土结构技术规程》JGJ3-2010； 1.2.17 《钢筋焊接接头试验方法标准》JGJ/T27-2001； 1.2.18 《火灾自动报警系统施工及验收规范》GB50166-92； 1.2.19 《建筑地基处理技术规范》（GB79-91-2001）； 1.2.20 《施工现场临时用电安全技术规范》(JGJ46-2005)； 1.2.21 《建筑施工高处作业安全技术规范》(GBJ80-91)； 1.2.22 《建筑机械安全技术规范》(GBJ33-2012) ； 1.2.23 《建筑施工扣件式钢管脚手架安全技术规范》(JGJ130-2011)、1.2.24 《钢筋机械连接通用技术规程》JGJ107-2010 2．工程概况 虚拟化操作手册2018年1月23日 目录 一、vsphere虚拟化管理 (3) 1) 虚拟化组成及介绍 (3) 2) ESXi (3) 3) 登录vcenter (8) 4) 新建虚拟机 (9) 5) 虚拟机的开启、安装操作系统和关闭 (22) 6) 安装VMTOOLS (26) 7) 更改虚拟机CPU和内存配置 (27) 8) 增加虚拟机硬盘 (31) 9) 虚拟机增加网卡 (37) 10) 新建portgroup (41) 11) 虚拟机在ESXI主机间迁移 (44) 12) 虚拟机在存储LUN间迁移 (47) 13) 克隆虚拟机 (49) 14) 倒换成模板 (52) 15) 模板倒换成虚拟机 (55) 16) 删除虚拟机 (58) 17) 对ESXi的物理主机关机维护操作 (59) 三、P2V转换 (61) 1) 安装Converter Server (61) 2) 登录Converter Server client (63) 3) Linux P2V (63) 4) Windows P2V (69) 一、vsphere虚拟化管理 1)虚拟化组成及介绍 Vsphere 包括vcenter和ESXI主机组成. 虚拟机运行在ESXI主机上。 ESXI系统安装在物理服务器上。 Venter是虚拟化的管理平台，它安装在一台虚拟机上。 2)ESXi 连接服务器，或者从HP服务器的iLo管理界面中，登录ESXi界面。 如果不是hp服务器可以用管理界面进行管理。或者直接到机房的物理服务器前进行如下操作 按F2，登录。 常用的操作就两块，网络和troubleshooting。 其中troubleshooting中的restart management agents选项，用在vcenter无法管理ESXi主机时。 JAVA保存计算过程的计算器课程设计 报告 1 2020年4月19日 保存计算过程的java计算器 目录 1 概述................................................................................. 错误!未定义书签。 1.1 课程设计目的 ............................................... 错误!未定义书签。 1.2 课程设计内容 ............................................... 错误!未定义书签。 2 系统需求分析 .................................................................... 错误!未定义书签。 2.1 系统目标 ....................................................... 错误!未定义书签。 2.2 主体功能 ....................................................... 错误!未定义书签。 2.3 开发环境 ....................................................... 错误!未定义书签。 3 系统概要设计 .................................................................... 错误!未定义书签。 3.1 系统的功能模块划分.................................... 错误!未定义书签。 3.2 系统流程图 ................................................... 错误!未定义书签。4系统详细设计 .................................................................... 错误!未定义书签。 5 测试 .................................................................................... 错误!未定义书签。 5.1 测试方案 ....................................................... 错误!未定义书签。 5.2 测试结果 ....................................................... 错误!未定义书签。 6 小结 .................................................................................... 错误!未定义书签。参考文献 ............................................................................... 错误!未定义书签。附录.................................................................................... 错误!未定义书签。 莲塘一中保集半岛学校工程高空作业 专 项 施 工 方 案 编制人： 审核人： 批准人： 江西建工笫四建筑有限责任公司 2015年3月8日 目录 1．工程概况 (1) 2．编制依据 (1) 3．安全施工措施 (1) 4．物料提升机安装和拆除作业 (5) 5．外脚手架搭设和拆除作业 (5) 6．模板工程作业 (6) 7．高处作业 (6) 8. 钢筋绑扎时的高空作业 (6) 9．混凝土浇筑时高空作业 (6) 10．悬空进行门窗作业 (7) 11．悬挑式钢平台作业 (7) 12. 组织机构及责任人 (8) 高空作业安全施工方案 一、工程概况： 工程名称：莲塘一中保集半岛学校 建设单位：南昌申标房地产发展有限公司 设计单位：江西省建筑设计研究总院 施工单位：江西建工第四建筑有限责任公司 监理单位：上海金品建设工程监理有限责任公司 莲塘一中保集半岛学校工程包含小学部综合教学楼和实验综合楼、初中部实验综合楼、行政办公楼、风雨操场、食堂、设备用房和看台工程等，位于莲塘一中保集半岛学校地块，芳草路以北，诚义路以西。小学部教学楼、初中部综合教学楼为框架结构/4层；行政楼为框架结构/5层；风雨操场、食堂、设备用房为框架/二层，风雨操场屋面为网架结构；总建筑面积约21371平米。 二、编制依据： 1、建筑施工安全检查标准 JGJ59-1999 2、建筑施工高处作业安全技术规范 JGJ80-91 3、龙门架及井架物料提升机安全技术规范 JGJ88-92 4、建筑施工扣件钢管脚手架安全技术规范 JGJ130-2001 5、建筑工程安全生产管理条例 6、中华人民共和国安全生产法 三、安全施工措施： （一）、安全管理措施：为了在该工程施工预防作业人员高空坠落 Vmware服务器虚拟化完整配置 VSPHERE 6.7虚拟化搭建及配置 Simon 目录 一、安装环境介绍 (3) 二、安装与配置vmware vsphere 6.7 (4) 1、安装vsphere 6.7 (4) 2、配置密码 (4) 3、配置DNS、主机名和IP地址 (5) 三、配置Starwind V8虚拟存储 (6) 四、使用windows 2012R2创建ISCSI存储 (9) 1、添加角色和功能 (9) 2、配置ISCSI链接 (10) 五、安装vcenter server 6.7 for windows (17) 1、安装vcenter server(自带嵌入式数据库) (17) 2、配置外部数据库SQL SERVER 2008 (22) 3、使用外部数据库安装Vcenter server (25) 六、安装Vcenter Server 6.7 for linux (29) 1、安装Linux版本的Vcenter (29) 七、创建数据中心和群集HA (42) 1、新建数据中心 (42) 2、创建群集HA (42) 八、添加ESXI主机和配置存储、网络 (44) 1、添加ESXI主机到群集中 (44) 2、配置存储 (45) 3、添加网络 (47) 九、创建虚拟机 (49) 1、上传镜像至共享存储 (49) 2、新建虚拟机 (49) 3、将虚拟机克隆为模板 (53) 4、通过模板部署新虚拟机 (55) 十、物理机迁移至ESXI（P2V） (60) 1、迁移windows物理机 (60) 2、迁移Linux物理机 (65) 3、使用Acronis BR迁移linux物理机 (66) 十一、vmotion迁移测试 (81) 十二、HA高可用测试 (83) 十三、VMware vSphere FT双机热备 (84) 十四、vSphere Data Protection配置部署 (86) 1、部署VDP模板 (86) 2、配置VDP (90) 3、创建备份作业 (96) 十五、部署vRealize Operations Manager (101) 1、部署ova模版 (101) 2、配置vRealize Operations Manager (104) 十六、部署VMware-vRealize-Log-Insight (110) 1、部署OVF模版 (110) 十七、附录 (117)简单的四则运算计算器程序
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