CN1169755A - A cylinder member and nickel-based facing - Google Patents
A cylinder member and nickel-based facing Download PDFInfo
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- CN1169755A CN1169755A CN 95196781 CN95196781A CN1169755A CN 1169755 A CN1169755 A CN 1169755A CN 95196781 CN95196781 CN 95196781 CN 95196781 A CN95196781 A CN 95196781A CN 1169755 A CN1169755 A CN 1169755A
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Abstract
In an internal combustion engine, a cylinder member, such as a valve, a seat portion, a piston or a cylinder liner, is provided with a welded high-temperature corrosion-resistant facing alloy. The hardness of the welded alloy has been increased by means of a precipitation hardening mechanism based on a solid-state phase transformation, where the temperature for activation of the precipitation hardening mechanism is above the operating temperature of the alloy. The precipiation hardening mechanism acts so slowly that the alloy substantially does not harden at the welding on to the cylinder member, but only hardens during a subsequent heat treatment at a temperature higher than the activation temperature for the precipitation hardening mechanism. Expressed in percentage by weight and apart from commonly occurring impurities, the nickel-based facing alloy comprises from 40 to 51 % Cr, from 0 to 0.1 % C, less than 1.0 % Si, from 0 to 5.0 % Mn, less than 1.0 % Mo, from 0.05 to less than 0.5 % B, from 0 to 1.0 % Al, from 0 to 1.5 % Ti, from 0 to 0.2 % Zr, from 0.5 to 3.0 % Nb, an aggregate content of Co and Fe of maximum 5.0 %, maximum 0.2 % O, maximum 0.3 % N and the balance Ni.
Description
The present invention relates at oil engine, particularly the cylinder member of large-sized two-stroke pinblock engine such as valve, seat partly, piston or cylinder sleeve, this member has anti-melting welding high temperature corrosion facing, and can about it, for example, melting welding is in the nickel-based facing of this cylinder member.
The many different facings that are used for the oil engine vent valve are known.For example, WO92/13179 narrates nickel-base alloy, Alloy50, cobalt base alloy, tungsten chromium cobalt 6, these wherein contain the purposes of the most important alloy compositions of 20-24%Cr, 0.2-0.55%C and 4-7%Al to reach nickel-base alloy.
EP-A-0521821 narration by have an Inconel625 melting welding layer or have one deck with the method for further not explaining, wherein except unavoidable impurities, also comprise 0.04-0.05%C, 47-49%Cr, 0.3-0.40%Ti, and all the other be valves that the nimonic of the Inconel671 of Ni is made.It mentions that alloy Inconel671 does not provide erosion resistance good as Inconel625, and it contains 20-22%Cr, 8.0-9.5%Mo, 3.15-4.15%Nb+Ta especially and all the other are Ni.
The DT-OS2446517 narration is used for the facing of nuclear reactor, trial is by being Ni by maximum 0.05%C, 1.0-5.0%Si, maximum 1.0%Mn, 20-50%Cr, 0.5-3.0%B, maximum 3.0%Cu, maximum 5.0%Fe and all the other, wherein the welding alloy that %Cr 〉=10 * %B+13 formed corrodes and avoid tying intergranular.Specific examples mentions having the alloy that scope is 1.13 to 2.86%B content.
The SE-B-422338 narration is used to have the valve of the oil engine that contains the wipla matrix, it is coated with to contain chrome-cobalt alloy in the temperature that surpasses 3000 ℃, so member is in the temperature receiver processing that is higher than processing temperature and aging, this purpose is the structure and size of stable alloy, and offsets the corrosion of knot intergranular.
DK-B-165125 narration is used for the vent valve of oil engine, and it has and comprises 13-17%Cr, 2-6%Al, 0.1-8%Mo, 1.5-3.5%B, 0.5-3%Ti, 4-7%Co and all the other are the resistance to high temperature corrosion facing of Ni.
Many other facings that are used for the vent valve of oil engine, by paper " operating experience of valve material summary at present " (Review of poerating experience with current valvematerials), it is known that nineteen ninety is published in from " the burning chamber of diesel engine material that the heavy fuel operation is used " (Diesel engine combustion chamber materilas forheavy fuel operation) book of London ocean engineer association.
Wherein, the purposes of valves known mask is for providing the surface on the member of the elevated temperature corrosion resistant with excellence, make this material in the heavy fuel oil diesel motor, do not corroded by high corrosive environment, and under the situation in present zone, the high rigidity surface is provided, and the formation of counteracting indenture, synchronous deposits has counteracting forms cold crack in material high ductility.
In known valve alloy, the hardness of mask is mainly by carbide guiding principle, boride and/or intermediate metal such as Ni in alloy substrate
3Al (γ '), μ-phase, σ-phase or Laves-precipitate mutually and provide by solution hardening.Known melting welding facing is exposed to cold cracking in melting welding postcooling member very much when the melting welding material, that is, melting welding crackle occurs after finishing immediately.The member cold cracking need be removed or be repaired to melt the weldering mask.The cold cracking problem is particularly in known boracic facing, because these known alloys have low-down ductility.B is used herein to the boride precipitation, to increase the hardness and the abrasion resistance of alloy.
Under the situation of mold member, in order to obtain good elevated temperature corrosion resistant, particularly containing under the sulphur and vanadium environment that derives from the heavy fuel oil products of combustion, the alloy of known use 50%Cr50%Ni type, or be IN657 type alloy that Ni formed by 48-52%Cr, 1.4-1.7%Nb, maximum 0.1%C, maximum 0.16%Ni, maximum 0.2%C+N, maximum 0.5%Si, maximum 1.0%Fe, maximum 0.3%Mg and all the other.Behind the mold, alloy comprise rich nickel γ-with rich chromium α-mutually, wherein decide on the Accurate Analysis of alloy, two-phase can be formed main dendritic crystal structure.Known these alloys are in the aging sclerosis of the service temperature that surpasses 700 ℃, and it causes at room temperature less than 4% ductile embrittlement feature.Because these relatively poor intensive properties, alloy only is used to intensity is not had the mold member of particular requirement.
EP-A-0529208 carries out the chromium base hard facing alloy that melting welding is used in valve seat area among being described in the valve of car engine.Alloy contains 30-48%Ni, 1.5-15%W and/or 1.0-6.5%Mo and all the other and is 40%Cr at least.Melting welding is carried out by laser melting welding, and contains chromium α-phase time at cooling curing, nickeliferous precipitation mutually.The involutory gold utensil of W and Mo has the solution reinforced effects, and helps very much to improve its intensity.C can 0.3-2.0% amount add, to increase hardness by the formation of carbide.And B can 0.1-1.5% amount add, increasing hardness by the formation of chromium boride, the amount that Nb can 1.0-4.0% adds, to form intermetallic compound and carbide and the boride that hardness obtains increasing.Therefore, containing the precipitation of chromium matrix and by in above alloy, carrying out solution hardening etc. and during melting welding, produce hardness of alloy immediately by carbide network, boride and/or intermediate metal at alloy.As a result, must give to pay close attention to fully and use special fusion welding method such as laser melting welding breaks when directly adopting fusion welding method avoiding.The melting welding large-scale component is used as large-scale marine engine, and wherein for example the valve cylinder member that can have a dish of diameter 300-500 millimeter almost can't be fit to commercialization.
Purpose of the present invention is for providing cylinder member and facing, it is to having high resistance in the thermal etching that is present in oil engine operation slot environment, simultaneously the risk of rupture relevant with melting welding is low more than known alloy, make the fusion welding method with suitable high melting rate can be used to commercial base with alloy melting welding on large-scale component.
About this purpose, the hardness that is characterized as welding alloy according to cylinder member of the present invention increases by the precipitation hardening mechanism of changing based on solid-state phase changes, the temperature of its activation precipitation hardening mechanism is higher than the service temperature of alloy, and its precipitation hardening mechanism acts on lentamente, make alloy non-sclerous in fact when cylinder member melting welding, sclerosis when still under the temperature of the activation temperature that is higher than precipitation hardening mechanism, heat-treating.
By mainly after the melting welding facing solidifies, change and cause hardness of alloy through the heat treated solid-state phase changes of material, used when solidifying in fact than the less eutectic precipitation of known alloy and mutually hard and obtain required hardness.So strengthen being combined between the main dendritic crystal throw out, it offsets thermal rupture.
Cold cracking after the melting welding is avoided satisfactorily, because slowly act on hardening mechanism only behind alloy stress relief, can increase hardness of alloy in follow-up heat treatment process, as following detailed description.Till when obtaining thermal treatment after member is finished machining, the melting welding facing is kept, for example, 25% high ductility, it prevents that unrelieved stress cracks after corresponding to the melting welding of the yielding stress of alloy.The yielding stress of the above-mentioned type facing increases with the increase of alloy rigidity, just like also increasing for the temperature that realizes stress relief.During being heated to the required activation temperature of hardening mechanism, melting welding, still very the ductile alloy is exposed to the mat stress relief and discharges under the temperature of unrelieved stress.Presclerotic low-alloy hardness causes stress to discharge fast and at low temperature.
Change in order to obtain solid-state phase changes, the alloy composition thing must be selected to make near selected analyzed area, principal element at the described alloy of phasor presents the inclination cut-off rule to the equilibrium state between two different regions, wherein, for example, a region can contain form crystal lattice BCC (body-centered cubic), and another contains the mixture of BCC and so-called FFC form (face-centered cubic).Can mention two FFC forms as for another example with mutual deflection side length.In melting welding pond fast setting and follow-up cooling, alloy does not have the time that the oneself is adjusted to equilibrium state, judges according to equilibrium state that promptly the ratio of a certain phase in the alloy is too big.Carry out follow-up heating being higher than stiffening temperature, on the phase that is deposited in undue embodiment mutually of failing to find full expression, its generation has the internal stress of crystallization distortion, and prevents that dislocation from stretching to whole crystalline particles, and makes alloy obtain high rigidity.One takes place through the diffusion of alloy composition to the conversion of another phase, and produces quite little some throw out, and its fine distribution makes the alloy that generates have microhardness very uniformly.These solid-state phase changes are changed itself and are learnt by other alloys, but important feature of the present invention is, for the analysis of selected facing, the conversion spended time causes it not become in the time of passing through too much and is activated, and has been cooled to up to the melting welding material to be lower than stiffening temperature.Because the melting welding material is kept high ductility up to sclerosis,, and harden with this shape so cylinder member can be machined into final geometrical shape.
Cylinder member is preferably has mainly solidified facing when the melting welding of Ovshinsky phase, and it partly becomes ferritic phase at the temperature inversion that is higher than the required activation temperature of precipitation hardening mechanism.This ferrite BCC form is favourable with the precipitation that Ovshinsky FCC form forms for obtaining high rigidity, and it is very suitable about the facing that generally contains nickel and chromium, because binary Cr-Ni phasor has feature, the shape of the S-a little cut-off rule between rich nickel of Ovshinsky and richer chromium region.
The precipitation hardening activation temperature of alloy is suitable between 550 to 1100 ℃, is preferably 700 to 850 ℃, and meanwhile, the activation of precipitation hardening mechanism needs this activation temperature to surpass greater than 40 seconds, is suitable greater than 20 minutes.Use this hardening mechanism, the facing of cylinder member is particularly suitable for fusion welding method, and it has the advantageously high melting rate that is fabricated to for member, and is applicable to the service temperature of large-scale one-stroke pinblock engine cylinder member.If cylinder member is used for less engine, can select other temperature.
Be preferably, represent and except common impurity with weight %, the facing of cylinder member comprises 40 to 51%Cr, 0 to 0.1%C, less than 1.0%Si, 0 to 5.0%Mn, less than 1.0%Mo, 0.05 to being Ni less than 0.5%B, 0 to 1.0%Al, 0 to 1.5%Ti, 0 to 0.2%Zr, 0.5 aggregate content, maximum 0.2%O, maximum 0.3%N and all the other to 3.0%Nb, maximum 5.0%Co and Fe.
In currently known methods, high-content Cr promotes the corrosion property of nickelalloy in the relating operation environment.Welding alloy has better corrosion property of known hard mask and higher hardness than cylinder member 500 to 700 ℃ service temperature, and than with the better mechanical properties of trussell nickelalloy.Outside described Cr content range, the solid phase conversion can't obtain with proper method, because in the time can't reaching the restriction of lower Cr content range, activation temperature becomes too low, if surpass the Cr content range upper limit, the curing of alloy prolongs at interval, and main ferrite is deposited in firmly with mutually crisp, causes undesirable ductility decline.The amount of other alloying constituents decision cut-off rule is in the relevant exact positions between mutually of two of phasors, and optimum content of its expression Cr can be adjusted subtly by test, and when being known, obtains required sclerosis activation temperature at other alloy ingredients.
The content of B shows decisive role astoundingly for the heat sealability of the nickelalloy with high-Cr.A small amount of B as 0.05% causes the curing of melt to be solidified into dendritic crystal curing by honeycomb, wherein the dendritic crystal branch is staggered and produce the geometric shape of structure component, so that in the end avoid further extending and occurring the plane rete in the solidified melt.Therefore, the content of B helps alloy to present high resistance to hot tearing in fact when melting welding.B is insoluble to γ and α-mutually very much, and its supposition is solidified and related to the eutectic mixture with many borides.When B content at least 0.5% the time, eutectic mixture has destructive degree with the required ductility that the boride amount of following increases to alloy.High-load B also causes the precipitation with high-intensity known and unwanted low melting point eutectic mixture.
Nb influences the solid phase conversion and provides nodular precipitation but not the thin layer precipitation, the ductility of residual alloy after its increase thermal treatment.It has importance to the cylinder member that operation the time is exposed to mechanical influence especially.Use Ta, Ti and Zr can get corresponding effect, but Ta is very expensive, and surpasses 1.5%Ti and can cause intermetallic precipitations to make alloy when melting welding, partly harden and become fragile, and surpass 0.2% Zr content and cause hot tearing takes place when melting welding.
Mo content less than 1.0% helps to strengthen the Ovshinsky phase through the solution reinforced effects, and it gives alloy bigger tensile strength.
Therefore Si, Mn and Al have the deoxidation effect when melting welding, become required composition in the filler that uses when the melting welding for fear of the melting welding defective.Though some deoxidation agent are burnt when melting welding, part residues among the final alloy.Wish that restriction Si to being less than 1%, must add a large amount of B because Si reduces the required effect of B.Mn is an effective oxygenant, and wishes that limiting its maximum is 5%, so that do not dilute the active ingredient of final alloy.Al content above 1% can cause intermetallic phase Ni
3Undesirable precipitation takes place in Al, and it can increase the hardness of Ni-based matter in fusion process.
C is the common impurity in the commercial alloy, and removes C cost costliness fully.C content should be limited to maximum 0.1% and form to avoid or to reduce carbide.O and N generally are deposited on alloy by ambient air, but it does not have help to required character.
Co and Fe also are impurity, wish it is limited to the aggregate content of maximum 5%.
The invention still further relates to nickel-based facing, it is characterized by according to the present invention, represent and except common impurity with weight %, it comprises 40 to 51%Cr, 0 to 0.1%C, less than 1.0%Si, 0 to 5.0%Mn, less than 1.0%Mo, 0.05 to being Ni less than the aggregate content of 0.5%B, 0 to 1.0%Al, 0 to 1.5%Ti, 0 to 0.2%Zr, 0.5 to 3.0%Nb, maximum 5.0% Co and Fe, maximum 0.2% O, maximum 0.3%N and all the other.As mentioned above, but the distinguishing characteristics of this alloy is to have very good elevated temperature corrosion resistant and reaches heat sealability and do not have any risk of rupture, and for example be, high rigidity under 650-800 ℃, have that ductility keeps and can be by thermal treatment, this ductility promotes alloy to be used on the machinery burden member.Discrete component to the influence of alloy property as mentioned above.
About determining the high ductility of alloy after melting welding, be preferably, the content of Al is 0.1% to the maximum, and the content of Ti is preferably maximum 0.1%.The Al of this low levels and Ti increase with ductility like this in hardness and reduce intermetallic phase Ni
3In the fusion process of Al (Ti), suppress precipitation.
The Cr content of alloy can be suitably between 45 to 50%.Minimum 45% Cr content provides precipitation hardening mechanism to reach the advantage that takes place with more controlled method under high activation temperature, it represents partly that alloy is cooled to apace and is lower than activation temperature that part represents that the process that member is machined to final geometrical shape can need not to consider to carry out under the heated condition of member mat machining to a great extent when melting welding.50% the upper limit provides suitable guarantee for the formation that prevents hard and the main ferritic phase of fragility.
In preferable specific embodiments, alloy contains 0.15 to 0.40%B, preferably is 0.25%B to the maximum.The upper limit of 0.4%B provides suitable guarantee, allow to increase the boride amount that ether is not big when alloy the solidifies precipitation of hardness, and 0.15% lower limit is when guaranteeing in the welding material to be diluted by the member base substance, and boron content does not become to be low to moderate at regional area and is easy to take place hot tearing.Boron produces required dendritic crystal structure in alloy ability descends along with CR content in the alloy and reduces.Less than 45% o'clock, therefore B content be preferably 0.20 to 0.30% at Cr content.0.25% this preferable upper limit in having the alloy of 45%Cr at least for suitable.
For fear of relatively large B is added in the alloy, the content of Si in welding alloy is preferably maximum 0.03%, and because as mentioned above, the content of Mn has dilution effect, and Mn content can suitably be limited to maximum 0.5%.Since same reasons, preferred maximum 0.5%Mo content.And/or the aggregate content of maximum 1.0%Co and Fe and maximum 0.02%O and maximum 0.02%N.
If Nb content minimum 1.0%, the favourable change that hardening mechanism takes place with nodular precipitation strengthens, and, quite suitably being limited to 2.0% in the content of Ang Gui Nb for the reason of economy, its reason is the higher Nb content character of modified alloy not in fact usually.Hot tearing danger can suitably limit in alloy by adding maximum 0.02%Zr when melting welding.
Now, examples of alloys of the present invention is by describing in detail with reference to the accompanying drawings, wherein
Fig. 1 shows the phasor of binary Cr-Ni system,
Fig. 2 and 10 has 48%Cr and all the other penetration tests for the reference alloy of Ni, reaches the photo that grinds with 500 times of the amplifications of polishing sample,
Fig. 3-6 is the corresponding photo of demonstration boron to the influence of alloy melting welding power with 11-14,
Fig. 7-9 is the corresponding photo of demonstration silicon to the influence of alloy melting welding power with 15-17,
Figure 18 and 24 has 43%Cr and all the other corresponding photos for the reference alloy of Ni.
Figure 19-23 is the corresponding photo of boron to the influence of this alloy melting welding power with 25-29, and
Figure 30-32 amplifies 1000 times photo according to the grinding of three kinds of alloys of the present invention with the polishing sample.
The a little S-shape that binary phase diagraml shown in Figure 1 is presented between equilibrium phase γ and the γ-α is cut apart Line. Cut-off rule begins at about 1345 ℃ of points by about 47%Cr, and extends downward obliquely The point of 500 ℃ of about 38%Cr. When the melting welding of the Ni-Cr of above-mentioned zone alloy, the consolidating of melting welding pond Change and later cooling take place rapidly, and form main Ovshinsky nickel phase γ. In follow-up sclerosis, Ferrite α-phase is deposited in the nickel phase as the nodular precipitation thing of very trickle distribution. Close for having other The alloy of gold composition, decide on type and the amount of all alloying components certain position of cut-off rule.
Because the melting welding power of alloy is key character of the present invention, carried out many tests with understand B with For example how the addition of the deoxidation composition of Si affects melting welding power. Test is molten with plasma transferred electric arc Weldering (PTAW) is carried out at 135 millimeters alloy-free steel dish with 30 millimeters of thickness of diameter. The melting welding ginseng Number is 30 volts arc voltage and 160 amperes current density. Melting welding speed is 60 mm/min, And melting rate is 1.6 kilograms/hour. The melting welding member is coated with redness and penetrates liquid, and it is at the wiping structure Residue in behind the part in any crackle, but the situation of so just can visual examination breaking. Member gets one separately Individual sample, and grind and polish and use microphotograph. Result of the test is shown in accompanying drawing.
Has the nickel alloy of high-load Cr at present owing to hot tearing danger seriously is regarded as being very difficult to Melting welding, it is confirmed in two reference tests. Fig. 2 and 11 show since hot tearing cause known seriously break. Figure 10 and 24 shows that curing takes place cellularly, and the dark space extension crystallization is intergranular The plane rete.
Boron becomes obvious to the appreciable impact of hot tearing by Fig. 3-6 and Figure 19-23. Respectively have 48 %Cr and 0.06%, 0.12%, 0.23% and the alloy of 0.40%B content can see long heat Crackle is adding few disappearance to 0.06%B, and the sample with 0.4%B does not break fully. Respectively have 43%Cr and 0.15%, 0.2%, 0.3%, 0.4% and the alloy of 0.5%B content, Show that when B content is 0.15% hot tearing sharply reduces, but hot tearing is only when B content is 0.2% Remove fully, its expression alloy must when Cr content is low, have big content B. Figure 11-14 show that B makes alloy solidify with dendritic crystal structure. Figure 25 shows same effect, but only at figure 26 obtain this effect fully.
Fig. 7-9 and 15-17 show that each has the Si adding with 0.09%, 0.17% and 0.33% measurer, and respectively have 0.06%, 0.11% and 0.21% alloy of following B content. Can see Si and reduce the ability that B produces the dendritic crystal consolidated structures.
Embodiment 1:
Prepare alloy of the present invention, it has following analytical value: 48.6%Cr, 1.5%Nb, 0.67%Mn, 0.39%Si, 0.1%B, 0.01 2%C and all the other are Ni.Alloy with same procedure as mentioned above and melting welding on member, only two welding beads are applied to top of each other.Do not observe after the melting welding and break.After the melting welding, alloy is 200HV20 20 ℃ hardness measurement.Member then at 700 ℃ by thermal treatment 72 hours.After the thermal treatment, also do not observe and break.By measuring method HBW3000/15/10, alloy rigidity is measured as 511HV20 and 460HBW at 20 ℃.Be measured as 415HBW at 500 ℃, its demonstration alloy is kept quite favourable high rigidity at high temperature.Sample is with general method cutting, grinding and polishing.Figure 30 shows the photo of alloy, and it is very trickle to see the hardening agent structure immediately, though amplify through high power, the discrete structure composition still almost can't be distinguished.Embodiment 2:
Carry out correspondence test as mentioned above with the alloy with following analytical value: 48.6%Cr, 0.5%Nb, 0.67%Mn, 0.39%Si, 0.1%B, 0.012%C, 0.24%Co+Fe and all the other are Ni.Do not break no matter before or after thermal treatment, all observe.Before the thermal treatment, hardness measurement is 220HV20, and after thermal treatment, hardness is measured as 551HV20 and 460HBW at 20 ℃, and reaching at 500 ℃ is 415HBW.The alloy photo is shown in Figure 31.Embodiment 3:
Carry out correspondence test as mentioned above with the alloy with following analytical value: 48.6%Cr, 1.5%Nb, 0.67%Mn, 0.39%Si, 0.1%B, 0.012%C, 0.24%C0+Fe and all the other are Ni.Do not break no matter before or after thermal treatment, all observe.Before the thermal treatment, hardness measurement is 210HV20, and after thermal treatment, hardness is measured as 467HV20 and 451HBW at 20 ℃, and reaching at 500 ℃ is 401HBW.The alloy photo is shown in Figure 32.
These embodiment show that alloy has low-down hardness and inevitable high ductility after melting welding, and the remarkable increase of hardness and do not occur breaking when sclerosis.Alloy can be used as the corrosion protection mask and melting welding on the surface of the environment of contact engine internal combustion groove.In addition, hot hardness is very high, the melting welding hard facing alloy that makes alloy of the present invention be suitable as very much to be used for valve seat area.
In above description, the composition in the alloy of the present invention is all explained with weight %.
Claims (13)
1. the valve in a cylinder member such as oil engine, particularly the large-sized two-stroke pinblock engine, seat part, piston or cylinder sleeve, this member has anti-melting welding high temperature corrosion facing, the hardness that it is characterized by welding alloy increases by the precipitation hardening mechanism of changing based on solid-state phase changes, the temperature that wherein activates precipitation hardening mechanism is higher than the alloy service temperature, and precipitation is slow so that alloy is non-sclerous in fact when melting welding is on cylinder member through the mechanism effect firmly, hardens when still only carrying out subsequent heat treatment under the activation temperature that is higher than precipitation hardening mechanism.
2. the cylinder member of claim 1 is characterized by facing and mainly solidifies when Ovshinsky phase (γ) melting welding, and its part becomes ferritic phase (α) at the temperature inversion of the activation temperature that is higher than precipitation hardening mechanism.
3. claim 1 or 2 cylinder member, the precipitation hardening activation temperature that it is characterized by alloy is preferably 700 to 850 ℃ at 550 to 1100 ℃, and the reactivation process of precipitation hardening mechanism needs this activation temperature to surpass greater than 40 seconds, is suitable greater than 20 minutes.
4. each cylinder member in the claim 1～3, it is characterized by with weight percent and represent and except common impurity, the cylinder member facing also comprises 40 to 51%Cr, 0 to 0.1%C, less than 1.0%Si, 0 to 5.0%Mn, less than 1.0%Mo, 0.05 to less than 0.5%B, 0 to 1.0%Al, 0 to 1.5%Ti, 0 to 0.2%Zr, 0.5 to 3.0%Nb, maximum 5.0%Co and Fe aggregate content, maximum 0.2%O, maximum 0.3%N, and all the other be Ni.
5. nickel-based facing, it is characterized by with weight percent and represent and except common impurity, it comprises 40 to 51%Cr, 0 to 0.1%C, less than 1.0%Si, 0 to 5.0%Mn, less than 1.0%Mo, 0.05 to less than 0.5%B, 0 to 1.0%Al, 0 to 1.5%Ti, 0 to 0.2%Zr, 0.5 to 3.0%Nb, maximum 5.0%Co and Fe aggregate content, maximum 0.2%O, maximum 0.3%N, and all the other be Ni.
6. the facing of claim 5 it is characterized by Al content and be 0.1% to the maximum, and Ti content is 0.1% to the maximum.
7. claim 5 or 6 facing is characterized by this alloy and contain 45 to 50%Cr.
8. each facing in the claim 5～7 is characterized by this alloy and contains 0.15 to 0.40%B, is preferably maximum 0.25%B.
9. each facing in the claim 5～8 is characterized by this alloy and contains maximum 0.03%Si, and is preferably maximum 0.5%Mn.
10. each facing in the claim 5～9 is characterized by this alloy and contains maximum 0.5%Mo.
11. each facing in the claim 5～10 is characterized by this alloy and contains 1.0 to 2.0%Nb, and is preferably maximum 0.02%Zr.
12. each facing in the claim 5～11 is characterized by that the aggregate content of Co and Fe is 1.0% to the maximum in this alloy, and this alloy suitably contains maximum 0.02% and 0.02%N.
13. each facing in the claim 5～12, it is characterized by be used to melting welding in large two-stroke IC engine particularly at the propelling engine of ship or the cylinder member example exhaust valve of fixed generator.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE1402894 | 1994-12-13 | ||
| DK1428/94 | 1994-12-13 |
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| CN1169755A true CN1169755A (en) | 1998-01-07 |
| CN1080769C CN1080769C (en) | 2002-03-13 |
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| CN95196781A Expired - Fee Related CN1080769C (en) | 1994-12-13 | 1995-12-12 | A cylinder member and nickel-based facing |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN100532930C (en) * | 2004-03-24 | 2009-08-26 | 第一高周波工业株式会社 | Alloy-coated boiler part and method of welding self-fluxing alloy-coated boiler part |
| CN107414336A (en) * | 2017-08-19 | 2017-12-01 | 安徽鼎恒再制造产业技术研究院有限公司 | Gate valve built-up welding continuous casting casting rod and its welding procedure in high temperature corrosion medium |
| CN109139170A (en) * | 2017-06-28 | 2019-01-04 | 曼柴油机和涡轮机欧洲股份公司 | In the valve cup ring of the gas exchange valve for the integrated casting being made of hard cochrome |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| DK177071B1 (en) * | 2009-10-30 | 2011-05-30 | Man Diesel & Turbo Deutschland | Exhaust valve spindle for an internal combustion engine and a method of manufacture thereof |
| DK177487B1 (en) * | 2012-07-06 | 2013-07-15 | Man Diesel & Turbo Deutschland | An exhaust valve spindle for an exhaust valve in an internal combustion engine |
| DE102016115026B4 (en) * | 2016-08-12 | 2018-03-08 | Vdm Metals International Gmbh | Process for the production of roll-coated sheets and roll-coated sheets |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| DK166219C (en) * | 1991-01-23 | 1993-08-16 | Man B & W Diesel Gmbh | VALVE WITH HAIR PILOT |
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1995
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100532930C (en) * | 2004-03-24 | 2009-08-26 | 第一高周波工业株式会社 | Alloy-coated boiler part and method of welding self-fluxing alloy-coated boiler part |
| CN109139170A (en) * | 2017-06-28 | 2019-01-04 | 曼柴油机和涡轮机欧洲股份公司 | In the valve cup ring of the gas exchange valve for the integrated casting being made of hard cochrome |
| CN107414336A (en) * | 2017-08-19 | 2017-12-01 | 安徽鼎恒再制造产业技术研究院有限公司 | Gate valve built-up welding continuous casting casting rod and its welding procedure in high temperature corrosion medium |
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