CN1100152C - Copper alloy and method of mfg. same - Google Patents

Abstract

To provide a metallic material, in particular, brass, which is excellent in mechanical strength, cutting performance, ductility in hot working, and anticorrosion. Brass according to the invention is roughly classified into four types including ' alpha + gamma ', ' alpha + beta + gamma ', ' alpha + normal beta ' and ' alpha + reinforced beta '. Brass of alpha + gamma type is alpha + gamma at room temperature, and its alpha phase has an area ratio of 97 to 70 %. Brass of alpha + beta + gamma type is alpha + beta + gamma at room temperature, and its beta phase and gamma phase, respectively, have area ratios of 3 to 30 %. In these two types, the gamma phase contains 8 wt.% Sn or more. Brass of alpha + normal beta type is alpha + beta at room temperature, and its beta phase has an area ratio of 20 % or more. Brass of alpha + reinforced beta type is alpha + beta at room temperature, and its beta phase has an area ratio of 15 % or more, and its beta phase contains 1.5 wt.% Sn or more. Brasses of all the types are alpha + beta in recrystallization temperature region, and their beta phases have area ratios of 30 to 80 %. Average crystal grain sizes of alpha and beta are 15 mu m or less, and preferably 10 mu m or less. An average crystal grain of gamma has an average minor axis of 8 mu m or less, and preferably 5 mu m or less. Brasses of alpha + gamma and alpha + gamma + beta have an apparent Zn content of 37 to 46 wt.%, and an entire Sn content of 0.9 to 7 wt.%. Brasses of the other two types have an apparent Zn content of 37 to 44 wt.%.

Description

Copper alloy and manufacture method thereof

1, technical field

The present invention relates to metallic substance, its manufacture method and metal products.Though the present invention relates generally to the Cu-Zn series copper alloy, i.e. brass and manufacture method thereof, principle of the present invention is not limited only to brass.

2, background technology

Know that in the past unit elongation surpasses 1000% metallic substance, and aluminium and stainless steel are for example arranged.Its good ductility is to cause because the slip of crystal particle crystal boundary has relaxed distortion.The slip of crystal boundary is that 0.01/ second low speed external force is effective for Deformation velocity, so for such low speed external force, aluminium and stainless ductility are all good.But for Deformation velocity surpassed 0.1/ second the sort of high speed external force, intercrystalline slip can not effectively work, and crystal grain produces the result of excessive dislocation, caused fracture to take place.

In order to make it not rupture under this high speed external force, people know the heat energy that utilizes in the processing and are out of shape the energy of deformation that produces makes it recrystallize (dynamic recrystallization).Improving ductility by means of dynamic recrystallization, is practical to brass etc.

Brass in the past is that the unit elongation of 0.1/ second high speed external force can surpass 100% for Deformation velocity.But prior art is difficult to obtain than its higher ductility.Obtain the high ductibility under the high speed external force, must accelerate recrystallize speed.Its method is, when in order to increase the heat energy that causes recrystallize and to make it be in the condition of high temperature, before operating force Shang Shui worked, it is thick that crystal grain just becomes, and causes to add dynamic recrystallization can not occur man-hour.Yet the past is not apply operating force under the ultimate temperature of alligatoring at crystal grain, so further improve the required energy shortage of recrystallize speed.

In fact the brass purposes is a lot.Different purposes require the performance of brass also to have nothing in common with each other.For example, forging requires to have high ductility under above-mentioned high speed external force with brass material.And for example, be used for the brass of valve and water halter hardware etc. and water contact component, requiring has high corrosion resistance and anti-erosion to water.In addition, also require to have high strength and good cutting ability in the various uses.

Cu-Zn-Sn system and Cu-Zn series copper alloy as water there being good corrosion resistance have admiraltymetal rod (JIS C-4641) and high tensile brass rod (JIS C-6782) respectively.Wherein the erosion resistance of so-called brass mainly is meant Dezincification corrosion resistant.So-called Dezincification corrosion resistant is meant because of the ionization tendency of copper and zinc differently, and zinc is preferential stripping in water, zinc content reduces with the passing of time and gradually as a result, cause occurring the phenomenon that intensity reduces, when using brass to make the water contact component, this is an important problem.

About the improvement of erosion resistance, a kind of brass is disclosed in the public clear 61-58540 communique of spy, this brass is to have added Pb, Fe, Ni, Sb and P in the Cu-Zn-Sn series copper alloy, is actually the α phase.Open in the flat 6-108184 communique the spy and to disclose an Albatra metal-, this Albatra metal-is to add Pb, Fe, Ni, Sb and P after hot-extrudable or drawing in the Cu-Zn-Sn series copper alloy, and then forms the α phase after 30 minutes～3 hours in thermal treatment under 500～600 ℃ of temperature.These prior arts are not separated out mutually by the β that makes the erosion resistance extreme difference, in fact only form the α phase, and obtain good corrosion resistance.

But, in fact being above-mentioned traditional brass of α phase, its physical strength and cutting ability are all relatively poor.And all good existing brass of physical strength and cutting ability has the alpha+beta crystal structure.But, because of β phase erosion resistance extreme difference, so it is also poor to have traditional brass erosion resistance of alpha+beta crystal structure.In a word, prior art is difficult to make erosion resistance and intensity and cutting ability to have both simultaneously.

The object of the invention is to provide a kind of metallic substance that has excellent ductility under high speed external force.

The object of the invention also is to provide a kind of brass that has good ductility under high speed external force.

The object of the invention also is to provide a kind of brass with good corrosion resistance and good cutting.

Another purpose of the present invention is to provide all brass of excellence of various performances such as a kind of ductility, intensity, cutting ability and erosion resistance.

Other purpose of the present invention is to provide a kind of manufacture method of the brass that can achieve the above object.

Another object of the present invention is to provide the various characteristics all metal products and the brass ware of excellence.

3, disclosure of an invention

The metallic substance that belongs to first aspect present invention is a kind of like this material, and the distortion that has metallic crystal when being subjected to external force deformation disperses the crystal structure of generation, and the strain energy that is produced by distortion can become the required energy of metallic crystal recrystallize.Therefore, under the effect of high speed external force, distortion does not produce in the part but produces its huge strain energy dispersedly, and its huge strain energy makes it to produce recrystallize and eliminates dislocation.As a result, can obtain good ductility under the high speed external force.

The metallic substance manufacture method that belongs to second aspect present invention comprises following a kind of like this operation, the i.e. metallic crystal strain energy that deforms of external force when representing with SE because of hot-work, heating when representing by hot-work with TE can be when heat energy that metallic crystal is given,

The required minimum energy of metallic crystal recrystallize of SE+TE＞distortion

Under the necessary energy condition of thickization of crystal grain, metallic substance is carried out hot worked operation under TE＜no external force state.

When carrying out hot-work according to manufacture method of the present invention, do not make under the high temperature that ductility reduces though metallic substance is not heated to because of thickization of crystal grain, but condition can be regulated the distortion that causes because of external force is produced in metallic substance strain energy fully big, even under lower temperature, also can effectively carry out dynamic recrystallization (so-called strain energy can be inferred into the potential that dislocation has).An example of this condition is, with the crystal structure of the metallic substance of heat supply processing, is adjusted to and is subjected to external force to do the time spent distortion to disperse the state (said distortion disperses, and can infer to become to make the microcosmic displacement to disperse) that produces.Its result can realize not having thickization of crystal grain phenomenon during heating, and has good ductility because of producing the dynamic recrystallization effect in the material effectively under high speed external force when applying external force.

External force effect down distortion disperses a type of the crystal structure that produces, be to mix with crystalline firmly than soft junction is brilliant, and crystal grain is very small.The soft under external force crystallization of this crystal structure produces distortion, and (perhaps under the intercrystalline slip effect between soft crystallization and the hard crystallization) produces the soft crystallization of this distortion and move dispersion.This crystal structure may reside in the following material, promptly contains two kinds of metallic elements at least, the alloy of separating out soft crystallization phases and hard crystallization phases, and its typical case's representative is the brass of copper and zinc alloy form.As its specific examples, can enumerate in alpha+beta, alpha+beta+γ and α+γ type brass, crystal grain small (15 μ m or following).

Making the element solid solution of recrystallize speed in the soft crystallization that helps improving two kinds of metal alloys as described above (improving the speed of recrystallize with nucleus that produces), also is effective.The typical case of this element representative is, has the element of approximate atomic radius with above-mentioned two kinds of metallic elements, make it in soft crystallization, to produce the displaced type solid solution, and under the situation of brass, be Sn for example.

The brass that belongs to third aspect present invention should meet the following conditions: in the recrystallization temperature zone, have the alpha+beta crystal structure, and in the recrystallization temperature district,

(A1) β phase area ratio is 30～80%,

(A2) α mutually with β average crystal grain diameter mutually at 15 μ m or following, preferred 10 μ m or following,

(A3) α disperses to exist mutually.

The preferred embodiment of brass of the present invention has the good high temperature ductility that requires below satisfying in the recrystallization temperature district:

(1) under 1/ second Deformation velocity, not damaged when producing 100% distortion,

(2) under 0.1/ second Deformation velocity, not damaged when producing 200% distortion,

(3) under 0.01/ second Deformation velocity, not damaged when producing greater than 200% distortion, or

(4) under 0.001/ second Deformation velocity, not damaged when producing greater than 600% distortion.Brass with the past can not reach good like this ductility.And superplastic material (for example aluminium and stainless steel) the in the past high speed distortion such for above-mentioned (1) and (2), there is not good ductility.

Brass of the present invention can be divided into four kinds of " α+γ type ", " alpha+beta+γ type ", " α+conventional β type " and " α+reinforcement β type " in this manual.Have α+γ crystal structure under " α+γ type " brass normal temperature, and meet the following conditions at normal temperatures:

(B1) γ phase area ratio is 3～30%, and is preferred 5～30%,

(B2) α phase average crystal grain diameter is 15 μ m or following, preferred 10 μ m or following,

(B3) γ phase average crystal grain diameter (minor axis) is 8 μ m or following, preferred 5 μ m or following, and

(B4) on α phase boundary or grain, there is above-mentioned γ phase.Such brass cutting ability excellence.

" alpha+beta+γ type " brass has alpha+beta+γ crystal structure, and meets the following conditions at normal temperatures under the normal temperature:

(B1) α phase area ratio is 40～94%,

(B2) β amounts to 3～30% with γ area ratio mutually mutually

(B3) α is 15 μ m or following with β average crystal grain diameter mutually mutually, preferred 10 μ m or following, and

(B4) γ phase average crystal grain minor axis is 8 μ m or following, preferred 5 μ m or following.Such brass cutting ability is also excellent.

Such brass preferably also meets the following conditions at normal temperatures:

(B5) contain 8 weight % or above Sn at γ in mutually, and

(B6) above-mentioned γ surrounds the β phase mutually.So, erosion resistance and anticorrosion stress-resistant breaking property (SCC resistance) are also excellent.

" α+conventional β type " brass has the alpha+beta crystal structure, and meets the following conditions under the normal temperature under the normal temperature:

(B1) β phase area ratio be 20% or more than, preferred 25% or more than, and

(B2) α is 15 μ m or following with β average crystal grain diameter mutually mutually, preferred 10 μ m or following.This brass has excellent cutting ability and intensity.

Have the alpha+beta crystal structure under " α+reinforcement β type " brass normal temperature, and meet the following conditions at normal temperatures:

(B1) β phase area ratio be 15% or more than, preferred 20% or more than,

(B2) α directly is 15 μ m or following with β average crystal grain mutually mutually, preferred 10 μ m or following, and

(B3) β contains 1.5 weight % or above Sn mutually.Such brass, cutting ability, erosion resistance and SCC resistance are all excellent.

The suitable examples of which kind of type no matter when giving 400% distortion with 0.01/ second Deformation velocity in the recrystallization zone, all has not damaged good high temperature ductility, and also has the good characteristic shown in following (1)～(3) under the normal temperature.

(1) good cutting ability

With the round brass rod of cutting soon that meets the JIS C-3604 of Japanese Industrial Standards is benchmark, its cutting resistance coefficient be 80 or more than.

(2) good anti-corrosion

Stretch the technological standard JBMA T-303 of copper association according to Japan and carry out Dezincification corrosion when test, under the maximum dezincify depth of penetration direction situation parallel with machine direction, the maximum dezincify degree of depth is for being 100 μ m or following, perhaps, under maximum dezincify depth of penetration direction and the vertical situation of machine direction, the maximum dezincify degree of depth is 70 μ m or following erosion resistance.

(3) good SCC resistance

When exposure in the ammonia atmosphere gas of cylindrical sample above 14% ammonia soln was loaded after 24 hours, said sample not disruptive maximum stress was 180N/mm ²Or more than.

But which kind of traditional metallic substance all can not satisfy above-mentioned those conditions.For example, SPZ (zinc-aluminium) and the corrosion-resistant of aluminium in water, especially aluminium produce corrosion hole, and these metals are poor because of the cutting ability that is clamminess.

Belong to fourth aspect present invention the brass manufacture method, have and cast the operation of making brassing under the following conditions:

(1) the apparent zinc content of raw material composition is 37～46 weight %,

Setting rate when (2) casting is 5 * 10 ¹～10 ⁵K/ second, preferred 10 ²～10 ⁵K/ second, and

(3) speed of cooling after solidifying be not higher than under 400 degree second for 5K/

The brassing made from this method is because satisfy the condition in recrystallization temperature district of the brass of third aspect present invention, so have good high-temperature ductility.

Manufacture method of the present invention can also have and make the step that brass is extruded part, promptly after above-mentioned casting, in 480～650 ℃, preferably in 480～600 ℃ of temperature ranges, above-mentioned brassing is carried out high temperature extrude.Process of cooling after the extruding of this high temperature, preferably to be not less than the 0.4K/ speed of second, proceed to 400 degree or below.As a result, this brass is extruded the condition that part also satisfies the brass that belongs to third aspect present invention.

Manufacture method according to the brass of fifth aspect present invention has under following condition:

(1) extrusion temperature is 480～650 ℃, in preferred 480～600 ℃ of temperature ranges, and

Relative reduction in area when (2) extruding be 90% or more than, be preferably 95% be more than, the apparent zinc content brass material that is 37～46 weight % is carried out hot-extrudable, make the step that brass is extruded part.Also can be met the brass extrudate of the brass condition of the present invention the 3rd aspect according to this manufacture method.Speed of cooling after hot-extrudable, preferably to be not less than the 0.4K/ speed of second, proceed to 400 the degree or below.Utilize the cooling of this high speed, the crystal grain also not alligatoring of footpath of cooling back can obtain having the 15 μ m of one of feature of brass of the present invention or the crystal structure of following small grains.

This manufacture method can also further have and comprises the step of making brass forging, is about to the above-mentioned part reheat of extruding, and carries out high temperature forging under 480～750 ℃, makes the step of brass forging.This forge piece also satisfies the condition according to the brass of third aspect present invention.The Deformation velocity of high temperature forging, preferred more than 1/ second.In high speed high temperature forging process like this, not alligatoring of crystal grain diameter during forging.The speed of cooling of high temperature forging, preferably also to be not less than the 0.4K/ speed of second, proceed to 400 the degree or below.So, the also not alligatoring of cooling back crystal grain diameter can obtain 15 μ m or following small grains.

Utilize above-mentioned manufacture method to make under the occasion of " α+γ type " of the present invention brass, the condition that can select is: Sn content is 0.9～7 weight % in the brass material, high temperature extrude or high temperature forging after speed of cooling before reaching below 400 ℃ be 0.4～5K/ second.Perhaps, as additive method, also can after the high temperature forging operation, add a heat treatment step, be about to brass material Sn content and adjust to 0.9～7 weight %, heat simultaneously brass forging and insulation 30 seconds under 400～550 ℃ of temperature or more than, the speed with 0.4～5K/ second is cooled to 400 ℃ or following heat treatment step then.

Utilize above-mentioned manufacture method to make under the occasion of " alpha+beta+γ type " of the present invention brass, the condition that can select is: Sn content is 0.9～7 weight % in the brass material, high temperature extrude or high temperature forging after speed of cooling before reaching below 400 ℃ be 0.4～10K/ second.Perhaps also can change the speed of cooling of adjusting in the manner described above, and after the high temperature forging operation, add heat a treatment process, promptly heat brass forging, insulation 30 seconds under 450～550 ℃ of temperature or more than, the speed with 0.4～10K/ second is cooled to 400 ℃ or following such heat treatment step then.

Utilize above-mentioned manufacture method to make under the occasion of " α+reinforcement β type " of the present invention brass, the condition that can select is: Sn content is 0.5～7 weight % in the brass material, apparent zinc content is 37～44 weight %, reach below 400 ℃ behind the hot-extrudable or high temperature forging before speed of cooling be 5～1000K/ second.Perhaps also can change the speed of cooling of adjusting in the manner described above, and after the high temperature forging operation, add a heat treatment step, promptly heat brass forging and insulation 30 seconds under 475～550 ℃ of temperature or more than, be cooled to 400 ℃ or following heat treatment step with the speed that is not less than 5～1000K/ second then.

Manufacture method according to the brass of sixth aspect present invention, having apparent zinc content is the brass material heating of 37～44 weight %, refrigerative step then, and in order to make the cooled crystal structure of this brass material be selected from alpha+beta, alpha+beta+γ and α+γ type structure, control Heating temperature, heating hold-time and speed of cooling be the controlled step of one of them at least.For example, under same Heating temperature and the condition of heating hold-time, can control speed of cooling the slowest, comparatively fast and the fastest, so that obtain α+γ, alpha+beta+γ and alpha+beta structure respectively.

Copper alloy (is typical case's representative with brass) according to seventh aspect present invention has following good cutting performance and physical strength.That is to say, be benchmark with the round brass rod of cutting soon that meets the JIS C-3604 of Japanese Industrial Standards, the cutting resistance coefficient be 80 or more than, and 0.2% yield strength or yielding stress are not less than 300N/mm ²Past is not had both the copper alloy of good like this cutting ability and intensity.For example, though bronze has 80 or above cutting resistance coefficient, its 0.2% yield strength and tensile strength only are respectively 80 newton/mm ²With 220 newton/mm ²Because contain 79% above copper in the bronze, so its intensity generally is difficult to improve.One of method that improves bronze intensity is to increase Sn content.But Sn content one increases in the bronze, and the defective that is called shrinkage hole (bubble during solidification shrinkage) during casting will become seriously, and the result makes strength deterioration.In contrast, copper alloy of the present invention, especially brass make up mutually by copper and the good zinc of cutting ability with excellent corrosion resistance, can improve cutting ability and intensity.

Belong to the copper alloy (is typical case's representative with brass) of eighth aspect present invention, have following good SCC resistance.That is to say that place the ammonia atmosphere gas of 14% ammonia soln top to load on the cylindrical sample of copper alloy of the present invention and expose 24 hours, this sample not disruptive maximum stress is 180N/mm ²Or more than.In order to improve SCC resistance, must improve intensity and erosion resistance (though only so not enough).Among the present invention, utilize the characteristic of the copper of excellent corrosion resistance to improve SCC resistance.Point out that in passing bronze anti-stress ability is low, 100N/mm ²Viscous deformation will take place under the stress of the left and right sides.

According to the brass of ninth aspect present invention, have following good cutting performance and erosion resistance.That is to say, be as the criterion to cut round brass rod soon, the cutting resistance coefficient is not less than 80, and stretch the technological standard JBMA T-303 of copper association according to Japan and carry out Dezincification corrosion when test, when maximum dezincify depth of penetration direction is parallel with machine direction, the maximum dezincify degree of depth is 100 μ m or following, and perhaps when maximum dezincify depth of penetration direction was vertical with machine direction, the maximum dezincify degree of depth was 70 μ m or following.Point out in passing, cut the round brass rod corrosion-resistant soon, the maximum dezincify degree of depth when carrying out the test of above-mentioned Dezincification corrosion reaches about 200 μ m.

A kind of method that improves the brass cutting ability is, makes average crystal grain diameter be in 15 μ m or following, is preferably 10 μ m or following.In addition, preferably crystal structure is adjusted have α mutually and be present in this α mutually crystal boundary, than the soft or hard part of α phase.The said part mutually softer than α for example is other metal of Pb or Bi and so on.The said part mutually harder than α, for example have β mutually with γ mutually, FeSi or FeP and so on intermetallic compound, and the oxide compound of copper or magnesium etc.Alpha+beta is compared with the crystal structure of α+γ, because the two alternate difference of hardness of α+γ big than alpha+beta, so machinability is better.

In order not only to improve machinability, but also improve erosion resistance, can adopt following the whole bag of tricks.For example in α+γ crystal structure, make γ contain Sn mutually, it is effective preferably containing the above Sn of 8 weight %.And in the alpha+beta tissue, the element (for example Sn, Si, Al, Sb, Ge or Ga) that β is contained mutually improve erosion resistance is effective.Make it to contain under the situation of Sn, β in mutually the preferred 1.5 weight % of Sn concentration or more than.And, have the α phase, the β phase, the ratio β that surrounds β phase crystal grain has mutually more that the crystal structure of high corrosion resistance part also is effective.Said than the better part of β phase erosion resistance, for example be the γ phase that contains 8 weight % or above Sn.In the crystal structure of such alpha+beta+γ, in order to make γ mutually the embrittlement phenomenon does not appear, and preferably the minor axis with γ phase average crystal grain is limited in 8 μ m or following.

Brass after according to the present invention cutting ability and erosion resistance being improved can be used among the various uses, in water tube component.Brass of the present invention is because average crystal grain diameter is little, so low temperature ductility is not so good.But, in the water pipe purposes because and do not require martensite and shape memory alloy high low temperature ductility like that, so brass of the present invention can fully satisfy desired product quality.

The present invention will provide the various goods that use metal of the present invention or brass on the other hand.The present invention also will provide the producing apparatus of making metal of the present invention or brass use.

4, brief description of drawings

Accompanying drawing 1 is the schema of manufacturing process's example of expression brass ware.

Accompanying drawing 2 is the curves of ductility (deformation rate and Deformation velocity) trier result in the expression recrystallization temperature district.

Accompanying drawing 3 is axis side views of explanation cutting ability test method.

Accompanying drawing 4 is curves of corrosion resistant corrosion test result.

Accompanying drawing 5 is synoptic diagram of explanation corrosion resistant corrosion test method.

Accompanying drawing 6 is synoptic diagram of explanation anticorrosion stress-resistant bursting test method.

Accompanying drawing 7 is the middle mutually Sn concentration of expression β and is cooled to 400 ℃ of graphic representations that concern cooling time before.

Accompanying drawing 8A is the microphotograph of an embodiment crystal structure of expression the present invention " α+γ type " brass.

Accompanying drawing 8B is the moulded piece figure that makes of 8A with reference to the accompanying drawings.

Accompanying drawing 9A is the microphotograph of an embodiment crystal structure of expression the present invention's " alpha+beta+γ type " brass.

Accompanying drawing 9B is the moulded piece figure that makes of 9A with reference to the accompanying drawings.

Accompanying drawing 10 is schemas that an example of the present invention " α+γ type " or " alpha+beta+γ type " brass manufacturing and water contact component operation is used in expression.

Accompanying drawing 11 is schemas that an example of traditional brass manufacturing and water contact component operation is used in expression.

Accompanying drawing 12A represents to cast postcooling speed to be decided to be the microphotograph of forged forging 19K/ second with the brass crystal structure.

Accompanying drawing 12B is the moulded piece figure that makes of 12A with reference to the accompanying drawings.

Accompanying drawing 13A is the microphotograph that accompanying drawing 12A partly amplifies.

Accompanying drawing 13B is the moulded piece figure that makes of 12A with reference to the accompanying drawings.

Accompanying drawing 14A represents to cast postcooling speed to be decided to be the microphotograph of forged forging 1.3K/ second with the brass crystal structure.

Accompanying drawing 14B is the moulded piece figure that makes of 14A with reference to the accompanying drawings.

Accompanying drawing 15A is the microphotograph that accompanying drawing 14A partly amplifies.

Accompanying drawing 15B is the moulded piece figure that makes of 15A with reference to the accompanying drawings.

Accompanying drawing 16A is that expression high temperature is extruded the brass that contains Sn1.9 weight %, extrudes the microphotograph that brass square billet crystal structure is used in the forging made from the cooling of 30K/ speed second the back.

Accompanying drawing 16B is the moulded piece figure that makes of 16A with reference to the accompanying drawings.

Accompanying drawing 17A is the brass square billet that high temperature forging accompanying drawing 16A represents, forges the microphotograph of back with the brass forging crystal structure of 20K/ speed second cooling manufacturing.

Accompanying drawing 17B is the moulded piece figure that makes of 17A with reference to the accompanying drawings.

Accompanying drawing 18A is that expression high temperature pushes the brass that contains Sn2.3 weight %, the forging that make with the cooling of 30K/ speed second the extruding back microphotograph of brass square billet crystal structure.

Accompanying drawing 18B is the moulded piece figure that makes of 18A with reference to the accompanying drawings.

Accompanying drawing 19A is the brass square billet that high temperature forging accompanying drawing 18A represents, forges the microphotograph of back with the brass forging crystal structure of 20K/ speed second cooling manufacturing.

Accompanying drawing 19B is the moulded piece figure that makes of 19A with reference to the accompanying drawings.

Accompanying drawing 20 is to use the axis side view of the water tap example of brass manufacturing of the present invention.

Accompanying drawing 21 is to use the view profile of the water tap example of brass manufacturing of the present invention.

Accompanying drawing 22 is to use the view profile of another water pipe example of brass manufacturing of the present invention.

Accompanying drawing 23 is to use the view profile of other water pipe examples of brass manufacturing of the present invention.

Accompanying drawing 24 is the synoptic diagram with hot water machine example of the reducing valve made with brass of the present invention and surplus valve.

Accompanying drawing 25 is synoptic diagram of the reducing valve of expression accompanying drawing 24 hot water machines.

Accompanying drawing 26 is synoptic diagram of the surplus valve of expression accompanying drawing 24 hot water machines.

5, optimum implementation of the present invention

Cu-Zn is that the purposes of alloy is wide, is widely used as parts, tame electrical article, mechanical part, building materials, Gas appliance and optical element etc. that water tap and water pipe and so on contact with water.This Albatra metal-is not only all good in general characteristics such as intensity, low temperature ductility, hardness, cutting and grindings, and also all good aspect each characteristic such as the desired erosion resistance of the parts that contact with water, anti-erosion, anticorrosion stress-resistant disruptiveness.

A principle of the present invention is, closes for above-mentioned each characteristic is improved and is conceived to the characteristic that Cu-Zn is the alloy junction crystalline phase.Know in the past α, β are arranged, three kinds of crystallization phasess of γ.Though γ phase erosion resistance and intensity are excellent, but because fragility caused the past not attempt applying in a flexible way its characteristic greatly.β phase factor corrosion-resistant, the past is thought always and is unsuitable for as the parts that contact with water.Though the erosion resistance of α phase and low temperature ductility are excellent, but intensity and cutting ability are bad.Therefore, the past all is considered as the characteristic of crystallization phases changeless, does not attempt actively to change the characteristic of crystallization phases.At this situation, the inventor etc. just further investigate the principal element that above-mentioned each characteristic exerts an influence, and found that except the kind of crystallization phases, and grain size also is an important factor.According to this achievement in research, the first, can improve the characteristic of brass mutually by effectively utilizing γ.The second, particularly can improve the characteristic of brass by the characteristic that changes the β phase.The 3rd, utilize the crystal grain diameter method for optimizing can improve the characteristic of brass.

As for γ being separated out mutually and changing a kind of concrete means of β phase behaviour, can add Sn.But, be unsuitable for forging the brass material of usefulness because add Sn that high temperature ductility is reduced.For head it off, the inventor etc. have done further research with regard to high temperature ductility, and the result finds out: the 4th, and the optimizing of crystal grain diameter improves high temperature ductility.The 5th finds out, utilize with α mutually with β mutually the ratio of mixture method for optimizing can obtain β phase dynamic recrystallization, improve high temperature ductility thus.

The above-mentioned achievement in research of having applied in a flexible way in an embodiment of the present invention.Illustrate before the embodiments of the invention, be necessary to illustrate the characteristic of above-mentioned three kinds of crystallization phasess.Table 1 expression Cu-Zn is the characteristic of three kinds of crystallization phasess presenting of alloy (brass), and the characteristic of pure Cu, pure Zn and pure Sn.

Table 1

	Erosion resistance	Yield strength	Forging property (high temperature)	Forging property (low temperature)	Machinability	Normal temperature ductility	Remarks
								The α phase	○	△	△	◎	×	◎	Has similar quality with Cu
The β phase	×	○	◎	×	◎	△	Has similar quality with Zu
								β phase+Sn	Zero significantly improves	◎ improves 30%	◎	×	◎	△
The γ phase	◎	◎	○	×	○	×
								Pure Cu	Well	×	△	◎	×	◎
Pure Zn	Difference	○	×	×	◎	△
								Pure Sn	Well	○	×	×	○	×

As shown in table 1, pure Cu erosion resistance, and ductility and cold forging (easness of cryogenic forging) are though good under the normal temperature, yield strength and machinability (easness of cutting) are poor.Cu-Zn alloy (brass) in the practicality behind the extensive in the past employing interpolation Zn replaces.In the Cu-Zn alloy, crystal structure is different different because of the Zn addition.Apparent Zn content is in 37 weight % or when following, it is mutually single-phase to become α, and apparent Zn content is in 37 weight % or when above, β phase (alpha+beta or β) occurs.When apparent Zn content further increased, γ phase (alpha+beta+γ, α+γ, β+γ or γ) appearred.Even under the low situation of Zn real content, when adding Sn (equivalent of Zn equals 2) and carrying out specific heat treatment, apparent Zn content can increase and present the γ phase.Here said term " apparent Zn content " is meant, when Cu content (weight %) with A, Zn content (weight %) is with B, the Zn equivalent of the element (as Sn) of interpolation is with t, the content of this element (weight %) makes it " { (B+tQ)/(A+B+tQ) } * 100 " when representing with Q.

α phase alpha brass, though erosion resistance and cold forging are good, but yield strength and machinability are poor.By to wherein adding Sn, though can improve erosion resistance and yield strength, when the Sn addition reaches 2 weight % or when above, has the trend that makes it to become fragile on the contrary.β has the characteristic almost opposite mutually with α mutually, though promptly erosion resistance and cold forging are poor, but yield strength, forge hot (easness of high temperature forging) and machinability are good.The new discovery that researchs such as the inventor obtain is, by adding Sn in the β phase crystal grain, erosion resistance and yield strength all improve, and especially erosion resistance is almost brought up to the degree that is equal to mutually of single-phased alloy mutually with α.The suitable Sn addition of γ occurs when surpassing preset value.Though γ is crisp mutually, but erosion resistance and yield strength are good.

Here said " erosion resistance " mainly refers to the character of Dezincification corrosion resistant.So-called " Dezincification corrosion " is meant because of the ionization tendency of copper and zinc differently, and zinc is preferential stripping in water, and zinc content reduces as time goes by gradually, and the phenomenon that causes intensity to reduce is a problem when using Cu-Zn to be alloy.

At Cu-Zn of the present invention is in the alloy (brass), will have the above-mentioned different properties characteristic crystalline phase appropriate combination of (comprising the characteristic through improving), can make the crystal grain optimizing.Table 2A～2C represents the contrast situation of composition and each characteristic and the prior art brass (reference examples) of 19 kinds of brass embodiment of the present invention.

Table 2A

	Heat-treat condition is formed
												Temperature (%)	Method of cooling	Cu (％)	Pb (％)	Fe (％)	Sn (％)	P (％)	Ni (％)	Sb (％)	Zn (％)	Zn equivalent (%)
	Reference examples 1	500	Air cooling	61.3	2.0	-	0.3	0.08	0.05	0.03	36.2												38.50
Reference examples 2												500	Air cooling	60.8	2.4	0.2	0.5	0.10	-	-	36.0	39.00
	Embodiment 1	500	Air cooling	62.9	1.5	-	1.0	0.05	0.05	0.03	34.5												37.80
Embodiment 2												500	Air cooling	61.3	2.0	-	1.0	0.08	0.05	0.03	35.5	39.20
	Embodiment 3	500	Air cooling	60.8	2.4	0.2	1.5	0.10	-	-	35.0												40.00
Embodiment 4												500	Air cooling	59.6	1.8	0.1	3.0	0.05	-	-	35.5	42.10
	Embodiment 5	500	Air cooling	60.8	2.0	0.1	5.0	0.05	-	-	32.1												44.00
Reference examples 3												600	Air cooling	61.8	2.2	0.4	1.0	-	-	-	34.6	39.20
	Embodiment 6	600	Air cooling	60.0	2.0	0.3	1.5	-	-	-	36.2												41.50
Embodiment 7												600	Air cooling	60.0	2.0	0.3	2.0	-	-	-	35.7	42.00
	Embodiment 8	600	Air cooling	59.0	2.0	0.3	1.5	-	-	-	37.2												42.50
Embodiment 9												600	Air cooling	59.0	2.0	0.3	2.0	-	-	-	36.7	43.00
	Embodiment 10	600	Air cooling	58.0	2.0	0.3	2.0	-	-	-	37.7												44.00
Embodiment 11												600	Air cooling	59.0	2.0	0.3	2.5	-	-	-	36.2	43.50
	Embodiment 12	600	Air cooling	59.0	2.0	0.3	3.0	-	-	-	35.7												44.00
Reference examples 4												550	Air cooling	59.0	2.8	0.2	0.5	-	-	-	37.5	41.50
	Embodiment 13	550	Air cooling	58.4	3.0	0.2	0.2	-	-	-	38.2												41.80
Embodiment 14												550	Air cooling	58.1	3.0	0.2	0.3	-	-	-	38.5	42.10
	Embodiment 15	550	Air cooling	58.2	3.2	0.2	0.3	-	-	-	38.1												42.00
Reference examples 5												600	Water-cooled	58.9	2.0	-	0.4	0.08	0.05	0.03	38.5	41.30
	Embodiment 16	600	Water-cooled	60.6	1.5	-	0.8	0.05	0.05	0.03	37.0												40.10
Embodiment 17												600	Water-cooled	59.3	2.0	-	1.5	0.08	0.05	0.03	37.0	42.00
	Embodiment 18	600	Water-cooled	59.3	2.4	0.2	2.0	0.10	-	-	36.0												42.60
Embodiment 19												600	Water-cooled	62.2	1.8	0.2	3.8	0.05	-	-	32.0	41.60

Table 2B

	The γ phase		The β phase			The α phase
									Area ratio/occupancy ratio (%)	Sn concentration (%)	Area ratio/occupancy ratio (%)	(％)	Particle diameter (μ m)	Area ratio/occupancy ratio (%)	Sn concentration (%)	Particle diameter (μ m)
	Reference examples 1	1.0	11.0				98.0	0.19									20.1
Reference examples 2									2.0	13.0				97.0	0.25	21.5
	Embodiment 1	3.2	14.5				95.8	0.56									14.5
Embodiment 2									3.5	14.0				95.5	0.53	14.3
	Embodiment 3	7.0	14.0				92.0	0.57									14.4
Embodiment 4									13.0	15.8				86.0	1.10	9.5
	Embodiment 5	21.0	18.0				78.0	1.56									9.3
Reference examples 3									2	10	2	1.70	4	95.0	0.90	30.0
	Embodiment 6	4.5	11.6	12	2.05	8	82.5	0.68									10.0
Embodiment 7									9	11.3	13	2.01	6	77.0	0.75	9.8
	Embodiment 8	5	10.9	16	2.13	8	78.0	0.72									9.5
Embodiment 9									10	11.0	10	2.14	6	79.0	0.74	9.7
	Embodiment 10	10	9.8	24	1.87	10	65.0	0.70									8.9
Embodiment 11									15	11.0	8	1.80	6	76.0	0.86	9.2
	Embodiment 12	16	13.4	4	1.80	4	79.0	1.10									9.5
Reference examples 4										-	17.0			82.0	0.5	19.0
	Embodiment 13		-	25.6			73.4	0.2									7.6
Embodiment 14										-	23.1			75.9	0.3	10.1
	Embodiment 15		-	25.2			73.8	0.3									5.7
Reference examples 5											19.0	1.30		80.0	0.19	22.0
	Embodiment 16			23.0	2.50		76.0	0.30									9.5
Embodiment 17											25.0	3.10		74.0	0.98	9.7
	Embodiment 18			29.0	3.50		70.0	1.41									10.5
Embodiment 19											38.0	7.10		61.0	1.81	10.2

Table 2C

	Yield strength σ 0.2(N/mm 2)		Low temperature ductility (%)	Hardness (Hv)	High temperature ductility	Resistance coefficient	Erosion resistance	Erosion resistance	SCC resistance
										Reference examples 1	265	×	35.2	91	○	×	○	×	×
Reference examples 2	273	×	34.8	93	○	×	○	×	×
										Embodiment 1	308	○	25.3	102	×	×	○	○	○
Embodiment 2	314	○	23.8	105	○	×	○	○	○
										Embodiment 3	355	◎	21.7	112	○	○	○	○	○
Embodiment 4	365	◎	18.7	113	○	○	○	○	○
										Embodiment 5	378	◎	13.2	150	○	○	○	○	○
Reference examples 3	291	×	39.8	93	○	×	○	×	×
										Embodiment 6	330	○	16.9	122	○	○	○	○	○
Embodiment 7	352	◎	17.0	133	○	○	○	○	○
										Embodiment 8	356	◎	13.4	126	○	○	○	○	○
Embodiment 9	352	◎	13.0	133	○	○	○	○	○
										Embodiment 10	372	◎	11.5	147	○	○	○	○	○
Embodiment 11	350	◎	12.3	142	○	○	○	○	○
										Embodiment 12	362	◎	10.4	142	○	○	○	○	○
Reference examples 4	193	×	22.0	115	○	×	×	×	×
										Embodiment 13	369	◎	21.0	143	○	○	×	×	○
Embodiment 14	342	○	27.0	126	○	○	×	×	○
										Embodiment 15	366	◎	22.6	155	○	○	×	×	○
Reference examples 5	250	×	21.0	95	○	○	×	×	×
										Embodiment 16	355	◎	25.2	120	○	○	○	○	○
Embodiment 17	372	◎	21.6	121	○	○	○	○	○
										Embodiment 18	358	◎	20.8	124	○	○	○	○	○
Embodiment 19	380	◎	18.2	130	○	○	○	○	○

The feature of crystal structure is as follows among the embodiment 1～19.Embodiment 1～5 has α+γ crystal structure, and crystal grain is by refinement (15 μ m or following), and the γ of characteristic through improving is utilized effectively mutually.Embodiment 6～12, have alpha+beta+γ crystal structure, and crystal grain is by refinement, and the β of characteristic through improving is utilized effectively mutually with γ mutually.Embodiment 13～15, have the alpha+beta crystal structure, and crystal grain is by refinement.Embodiment 16～19 has the alpha+beta crystal structure, and crystal grain is by refinement, and by adding Sn the characteristic of β phase is improved.In addition, in these embodiment 1～19, the ratio of each crystallization phases is suitably adjusted.About after being described in more detail in of these embodiment crystal structures.

Embodiment 1～19, is under the creating conditions who meets the principle of the invention, and casting has the brass sample of forming shown in the table 2A, will carry out (concrete manufacturing sequence is shown in the accompanying drawing 1) of the method manufacturing of high temperature forging after its high temperature extruding.The heat-treat condition of table 2A～2C shows forging temperature and method of cooling.The speed of cooling of air cooling is 0.8K/ second, and the speed of cooling of water-cooled is 100K/ second.

For the characteristic of table 2A～2C, can enumerate " 0.2% yield strength (N/mm ²) " (produce 0.2% the required tensile stress of tensile-permanent set), " low temperature ductility (%) " (ductility in the machining at low temperature humidity province), " hardness (HV) ", " high temperature ductility " (high temperature process humidity province, i.e. ductility in the recrystallization temperature district), " cutting resistance coefficient ", " erosion resistance ", " erosion resistance " and " anticorrosion stress-resistant disruptiveness " (SCC resistance).

In table 2A～2C, show and estimate the label symbol that each characteristic is used.For " 0.2% yield strength ", not enough 300N/mm ²Be decided to be bad (*), 300 or above and not enough 350N/mm ²Be evaluated as good (zero), 350N/mm ²Or above be chosen as excellent (◎).With regard to " high temperature ductility ", with 10 ° of (/ second) Deformation velocitys,, do not produce disruptive maximum distortion rate, being chosen as of less than 100% bad (*), 100% or above be chosen as good (zero) to the result that sample carries out tension test.About " cutting resistance coefficient ", carry out the result of cutting test according to the aftermentioned mode, cut round brass rod (JIS C-3604) soon and be the cutting resistance coefficient of benchmark, being chosen as of less than 80 bad (*), 80 or above be chosen as good (zero).

" erosion resistance " stretched copper association technological standard (JBMA T-303) according to Japan and carried out the Dezincification corrosion test, and estimate according to the evaluation criteria of JBMA T-303 regulation.Promptly, maximum dezincify depth of penetration when dezincify depth of penetration direction is parallel with machine direction, at 100 μ m or following be chosen as good (zero), and the maximum dezincify depth of penetration when maximum dezincify depth of penetration direction is vertical with machine direction does not satisfy being chosen as of these standards bad (*) at 70 μ m or following be chosen as good (zero).

With regard to " erosion resistance ", under test conditions described later, do not leak required necessary mounting torque through not producing after 1500 hours, be in 0.8Nm or above be chosen as bad (*), this numerical value is following is chosen as good (zero).About " anticorrosion stress-resistant disruptiveness ", under test conditions described later, be chosen as bad (*) through disruptive after 24 hours, disruptive is not chosen as very (zero).

As shown in table 2A～2C, among the embodiment 1～5, yield strength, low temperature ductility, erosion resistance, erosion resistance, anticorrosion stress-resistant disruptiveness all are cited as very (zero) or excellent (◎). Embodiment 1 and 2 machinability are cited as bad (*), by inference its reason may be because do not satisfy γ be not less than mutually 3% and β be not more than 3% mutually, or γ is not less than the cause of 5% top condition mutually.Among the embodiment 1, high temperature ductility also is cited as bad (*), and its reason may be that apparent Zn contains quantity not sufficient 38 weight % by inference, and β does not mutually reach 30% and causes during hot-work.

All characteristics all is cited as very (zero) or excellent (◎) among the embodiment 6～12.

Except erosion resistance and erosion resistance, other characteristics all are cited as very (zero) or excellent (◎) in embodiment 13～15.The erosion resistance of embodiment 13～15 and erosion resistance are cited as bad (*), may be because do not comprise the γ phase of excellent corrosion resistance by inference, and β mutually in the cause of Sn concentration less than 1.5 weight %.

Embodiment 16～19, and all characteristics all is cited as very (zero) or excellent (◎).

The profitability of the embodiment of the invention below is described, especially the profitability aspect " high temperature ductility ", " cutting resistance coefficient ", " erosion resistance " and " anticorrosion stress-resistant disruptiveness ".

" high temperature ductility " profitability in embodiments of the present invention at first is described.High temperature ductility is good, is to supply with high temperature forging and so on hot-work one of most important properties of square billet.Accompanying drawing 1 an expression high temperature forging brass ware example of manufacturing process.

At first in step 1, mix electrolytic copper, electrolytic zinc and cutting metal, and carry out melting and casting.Follow in step 2, use the method for casting back chilling to make middle molding, heat this middle molding then, utilize extruding formation method to make bar-shaped or the wire blank.And then in step 3 cold rolling this bar-shaped or wire blank, anneal and pickling, cut into predetermined size.

The above-mentioned blank of heating in step 4 forges required characteristic so that guarantee to be suitable for next step then.And then the blank that will heat in step 5 places forging mold to forge.Cool off afterwards, as the preparation of step 6.In case stop cooling, just enter step 6, carry out pickling or sandblast, to remove lip-deep oxide film, further be shaped, obtain goods through cutting, after grinding and electroplate each operation.

Two embodiment (the inventive method 1 and the inventive method 2) of the manufacture method of the present invention of accompanying drawing 1 manufacturing process are adopted in the expression of table 3 and table 4, when adopting classical production process, create conditions and the contrast situation of goods crystal structure.

Table 3

	Apparent Zn content	Setting rate during casting	Speed of cooling after the casting	Extrusion temperature	Cooling after extruding
						The inventive method 1	41.5～46.0	5×10～10 5K/ second	To 5K/ below 400 ℃ more than second	480～550℃	Air cooling 0.4K/ is more than second
The inventive method 2	38.0～43.5	5×10～10 5K/ second	To 5K/ below 400 ℃ more than second	550～625℃	Air cooling 0.4K/ is more than second
						Existing method	39.0～43.0	3 * 10K/ second	To 0.5K/ below 400 ℃ more than second	650～750℃	Air cooling 0.3K/ is more than second

Table 4

In table 3, the ratio of mixture that is melted material in " apparent Zn content " and the step 1 shown in the accompanying drawing 1 is relevant, " setting rate during casting " is relevant with the casting condition of step 1 with " speed of cooling after the casting ", and " extrusion temperature " is relevant with the hot-rolled condition of step 2 with " cooling after the extruding ".In table 4, " crystal grain diameter " is meant, step 2 hot rolling stops the crystal grain diameter (crystal grain diameter of the finished product also becomes identical in the methods of the invention) of back square billet, " the β phase ratio during forging ", " forging temperature " " deformation rate and Deformation velocity " are relevant with the forging condition in the step 5, and " yield strength " and " α after the forging, β, γ be ratio mutually " are meant that step 7 makes the numerical value of product.

As shown in table 3, compare with traditional method, in the inventive method 1 and 2, the apparent Zn content of brass material higher (addition of Sn is higher in typical case), (speed of cooling during step 1) after setting rate and the casting is faster, and the temperature during hot rolling (step 2) is lower, and the speed of cooling after the extruding is faster (specifically for high temperature forging, be cooled to 400 ℃, with 0.4K/ second or above speed cooling).In addition, though table 3 do not illustrate, in method 1 of the present invention and 2, extruding section decrement be in 90% or more than, preferred 95% or more than.

With the square billet of the inventive method 1 and 2 preparations, as shown in table 4, compare with the square billet of traditional method preparation, under the temperature of ploughing, can forge (step 5) with more gross distortion rate and Deformation velocity.Its reason technical characterictic is by inference, and is as shown in table 4, the comparing of the square billets of the inventive method 1 and 2 preparations and traditional method preparation, and crystal grain diameter is littler, even and contain haggling over suitable proportion that high temperature ductility is also good under the low temperature β causes mutually.Can forge under lower temperature, be favourable from the few viewpoint of forging equipment deterioration.In addition, as shown in table 4, with the inventive method 1 and 2 forged products, it increases substantially than traditional forged article.

Accompanying drawing 2 expression the inventive method and traditional method make respectively the forging temperature district of two kinds of square billets (specifically, table 2A～2C illustrated embodiment 10 and reference examples 4) in high temperature ductility.Transverse axis is represented Deformation velocity ε (second ^-1), the longitudinal axis is represented deformation rate ε L (%).Compare with reference examples 4, embodiment 10 obviously has excellent high-temperature ductility more.

Below explanation " coefficient is formed in cutting " profitability in embodiments of the present invention.

The result that the reference examples 3 shown in 2A～2C, embodiment 8,10,11, quick round brass rod (JIS C-3604) and α phase alpha brass material carry out cutting test is just shown in table 5 expression.In cutting test, as shown in Figure 3,, measured main component with the periphery of lathe with 100 (meters/minute) and two kinds of friction-motion speed cutting circle cylindricality samples 1 of 400 (meters/minute).The cutting resistance coefficient of each sample is that each sample is to the machinability of main component, with respect to the best per-cent of cutting round brass rod master component soon of what is called.Table 5

As shown in table 5, embodiment 8,10 and 11 cutting resistance coefficient almost reach 90% of quick round brass rod with optimized cutting, and the numerical value of alpha brass is better mutually than reference examples 3 and α.

" erosion resistance " profitability in embodiments of the present invention then is described.

Result shown in accompanying drawing 4 expression table 2A～2C, embodiment 8,10 and the test of reference examples 4 erosion resistances; The method of this erosion resistance test of accompanying drawing 5 expressions.In erosion resistance test, as shown in Figure 5, use inner porose 7 cylinder shaped test piece 5, with 40 meter per second speed water is passed through after this hole to schedule, 4.9 * 10 ⁵Pa (5Kg/cm ²) under the hydraulic pressure, measure mounting torque to the required resin plug 9 of sealing gap 7.As shown in Figure 4 as can be known, embodiment 8,10 compares with reference examples 4, has better erosion resistance.

Specification sheets " anticorrosion stress-resistant disruptiveness (SCC resistance) " is to the profitability of the embodiment of the invention then.

In the SCC resistance test, as shown in Figure 6, in the glass moisture eliminator, under the state to cylinder shaped test piece 13 vertical loading, exposure was observed the disruptive production after 24 hours in the nitrogen vapor atmosphere.Table 6 expression, the test-results of embodiment 8,11,15 shown in table 2A～2C and reference examples 4 (principle stress and break between relation).As shown in Table 6, compare with reference examples 4, embodiment 8,11,15 has better SCC resistance.

Table 6

Principle stress (N/mm 2)	38	87	121	155	189	223	258	292	327	355
											Embodiment 11	○	○	○	○	○	○	○	○	○	×
Embodiment 8	○	○	○	○	○	×	×	×	×	×
											Embodiment 15	○	○	○	○	○	×	×	×	×	×
Reference examples 4	○	×	×	×	×	×	×	×	×	×

Zero: crack-free *: break

As mentioned above, the embodiment 1～19 shown in table 2A～2C has good characteristic.Such just as already explained, crystallization refinement in the alpha+beta crystal structure of embodiment 16～19 (15 μ m), and utilize the method for adding Sn in mutually at β to improve characteristic is called this type " α+reinforcement β type " below in the brass of the present invention.Embodiment 1～5, and grain refining in α+γ crystal structure, and utilize γ to improve characteristic mutually below is called this type " α+γ type ".Embodiment 6～12, and grain refining in alpha+beta+γ crystal structure, and utilize γ to improve characteristic mutually below is called this type " alpha+beta+γ type ".Embodiment 13～15, utilize the method for crystal grain diameter refinement in the alpha+beta crystal structure to improve characteristic, so following it is called " α+common β type ".

Below will describe the crystal structure and the method for making of three types of brass of the present invention in detail.

At first explanation " α+reinforcement β type ".There is the β phase that contains 1.5 weight % or above Sn in such tissue at the intergranule of α phase.

Table 7 lists 7 kind brass sample No.1～7 relevant with " α+reinforcement β type " (with showing the different brass that 2A～2C enumerates).

Table 7 expression, the result of middle mutually Sn concentration of the composition of sample No.1～7, apparent Zn content, β and erosion resistance (Dezincification corrosion resistant) test.The Sn concentration of β in mutually uses the method for thermal treatment and cooling process to adjust, and has done quantitative analysis with EPMA.The evaluation of erosion resistance is according to carrying out with regard to showing the same way as that 2A～2C illustrated.

Table 7

No.	Form (wt%)								Zn content apparent (wt%)	The middle mutually Sn concentration (wt%) of β	Erosion resistance
													JBMA tests the maximum Dezincification corrosion degree of depth (μ m)	Judge
											Cu	Pb			Fe	Sn	P	Ni	Sb	Zn
	1	61.3	2.0	-	1.0	0.08	0.05	0.03														35.5	39.2	1.3	120	×
2									60.8	2.4	0.2	1.5	0.10	-	-	35.0	40.0	1.4	100	×
	3	61.3	2.0	-	1.0	0.08	0.05	0.03													35.5	39.2	1.7	29	○
4									60.8	2.4	0.2	1.5	0.10	-	-	35.0	40.0	2.2	37	○
	5	60.8	2.4	0.2	1.5	0.10	-	-													35.0	40.0	3.3	20	○
6									59.6	1.8	0.1	3.0	0.05	-	-	35.5	42.1	4.0	10	○
	7	62.9	1.5	-	0.5	0.05	0.05	0.03													35.0	37.3	1.5	55	○

Table 7 explanation, Sn concentration and the erosion resistance of β in mutually is closely related.That is to say, obtain good anti-corrosion make the Sn concentration of β in mutually reach 1.5 weight % or above be necessary.In the table 7, this condition is satisfied in sample No.3～7, and these brass belong to " α+reinforcement β type ".Point out in passing, reach in 1.5 weight % or the above this brass in the Sn concentration of β in mutually, all Sn concentration of alloy be 0.5 weight % or more than, apparent Zn content is 37 weight % or above and 44 weight % or following.

Thermal treatment of carrying out in manufacturing process and hot worked condition (for example, speed of cooling, thermal treatment temp and heat treatment time) exert an influence to the Sn concentration of β in mutually.Accompanying drawing 7 is that the expression thermal treatment temp is under 550 ℃ the situation, and the cooling time that the arrival after the thermal treatment is 400 ℃ is with the curve that concerns experimental result between the concentration of the Sn of β in mutually.Accompanying drawing 7 explanation reaches 0.4K/ second or above (zone in (1) some left side in the accompanying drawing 7) if begin to cool down to 400 ℃ speed of cooling, then the Sn concentration of β in mutually reach 1.5 weight % or more than.Utilize further test to determine, the upper limit of speed of cooling at least can be up to 1000K/ second.In addition, thermal treatment temp is not only under 550 ℃ occasion, even under the situation of other thermal treatment temp of 510 ℃ and so on, also obtained experimental result same as described above.

Table 8 expression thermal treatment temp (specimen temperature during thermal treatment) and heat treatment time (heat treated hold-time) are to Sn concentration and the area ratio/occupancy ratio of the β phase experimental studies results that influence of β in mutually.

Table 8

Thermal treatment		The middle mutually An concentration (wt%) of β	β phase area occupation rate (%)
				Temperature (℃)	Time
475℃	30 seconds 1 minute 8 minutes 15 minutes 30 minutes					1.6 1.9 2.3 2.5 2.5	40 40 35 30 25
		500℃	30 seconds 1 minute 8 minutes 15 minutes 30 minutes	1.6 2.1 3.2 3.4 3.6	40 35 25 20 15
525℃	30 seconds 1 minute 8 minutes 15 minutes 30 minutes					1.7 2.1 3.2 3.5 3.8	40 35 25 20 15
		550℃	30 seconds 1 minute 8 minutes 15 minutes 30 minutes	1.7 2.2 3.2 3.3 3.5	35 30 20 15 10

(speed of cooling: to 400 ℃ is 5～1000K/ second)

Table 8 explanation, thermal treatment temp is high more, and perhaps heat treatment time is long more, and the Sn concentration of β in mutually is just high more.On the other hand, thermal treatment temp is high more, and perhaps heat treatment time is long more, and the occupation rate of β phase area is just low more.And to be in 475～550 ℃ and heat treatment time be in 30 seconds or the above scope to the thermal treatment temp shown in the table 8 at least, the Sn concentration of β in mutually can reach 1.5 weight % or more than.When prolonging heat treatment time, though the Sn concentration increase of β in mutually improves erosion resistance, heat treated economy consideration from manufacturing process, heat treatment time preferably is no more than 3 hours.

Below " α+γ type " of the present invention and the brass of " alpha+beta γ+type " are described.

Accompanying drawing 8A is the microphotograph of the No.7 of brass sample shown in the aftermentioned accompanying drawing 3 crystal structure.Accompanying drawing 8B is the crystal structure moulded piece figure that makes of 8A with reference to the accompanying drawings.

Accompanying drawing 9A is the microphotograph of the sample of brass shown in the table 9 No.4 crystal structure.Accompanying drawing 9B is the moulded piece figure of the crystal structure made of 9A with reference to the accompanying drawings.

In the crystal structure shown in the accompanying drawing 8A, γ phase (the black part among the figure) is separated out growth at the crystal boundary of α phase crystal grain (white portion among the figure), and β almost disappears mutually.The representative instance of " α+γ type " at this moment of the present invention.In the crystal structure shown in the accompanying drawing 9A, contain α mutually with β mutually, separate out γ phase (part of black among the figure) on the crystal boundary of (among the figure less white portion) crystal grain mutually at α phase (among the figure bigger white portion) and β, β is surrounded mutually.Typical case's representative of " alpha+beta+γ type " at this moment of the present invention.It is the littlest with β median size mutually mutually that the median size of γ phase (being the mean value of minor axis in this case) cans be compared to most α, 8 μ m or following for example, preferred 5 μ m or following.

Table 9 lists 7 kinds of relevant brass sample No.1～No.7 with " α+γ type " of the present invention or " alpha+beta+γ type ".The result of the composition of table 9 expression sample No.1～No.7, apparent Zn content, γ phase area occupation rate and erosion resistance (Dezincification corrosion resistant) test, and the Sn concentration of expression γ in mutually.Corrosion resistance test is according to carrying out with regard to the same procedure of showing 2A～2C explanation.

Table 9

No.	Form (wt%)								Apparent Zn content (wt%)	γ phase area occupation rate (%)	Erosion resistance		The middle mutually Sn concentration (wt%) of γ
														JBMA tests the maximum Dezincification corrosion degree of depth (μ m)	Judge
											Cu	Pb				Fe	Sn	P	Ni	Sb	Zn
	1	61.3	2.0	-	1.0	0.08	0.05	0.03															35.5	39.2	0.4	120	×	11.4
2									60.8	2.4	0.2	1.5	0.10	-	-	35.0	40.0	1.8	100	×	10.5
	3	61.3	2.0	-	1.0	0.08	0.05	0.03														35.5	39.2	3.3	50	○	12.3
4									60.8	2.4	0.2	1.5	0.10	-	-	35.0	40.0	4.2	37	○	11.8
	5	60.8	2.4	0.2	1.5	0.10	-	-														35.0	40.0	9.9	20	○	9.5
6									58.0	2.4	0.3	3.0	0.05	-	-	36.3	45.0	20.0	10	○	8.9
	7	62.9	1.5	-	0.9	0.05	0.05	0.03														34.2	37.3	3.0	55	○	15.6

Table 9 explanation, if γ phase area occupation rate be in 3.0% or above and 20% or following scope in, then can obtain good anti-corrosion.In the table 9, sample No.3～No.7 satisfies this condition, belongs to " α+γ type " of the present invention or " alpha+beta+γ type ".And distinguish that then high temperature ductility is also good if satisfy above-mentioned condition.

Thermal treatment of carrying out in the manufacturing process or pyroprocessing condition (for example thermal treatment temp and speed of cooling), influential to γ phase area occupation rate.A manufacture method example of accompanying drawing 10 expressions brass ware of the present invention.In the manufacture method of accompanying drawing 10 expressions, it is brass material that sample No.3～No.7 etc. has the Cu-Zn-Sn that forms shown in the table 9, is shaped through high temperature forging and hot rolling etc.And then this molding carried out keeping 30 seconds or above thermal treatment under 400 ℃ or above and 550 ℃ or the following temperature, with 0.4K/ second or above and 10K/ second or following speed this molding is cooled to 400 ℃ then.Utilize this thermal treatment and cooling, the crystal structure of molding is become " α+γ type " or " alpha+beta+γ type ".This molding carried out machining, grinding and plating etc. thereafter.

Point out that in passing in traditional general manufacture method, as shown in Figure 11, when adopting the method for cast form, it is quite a lot of to cast required operation.And in the inventive method shown in the accompanying drawing 11, utilize methods such as high temperature forging and hot rolling to be shaped, so compare with traditional method, the operation number will reduce.

The experimental result that concerns between table 10 expression γ phase area occupation rate and the heat-treat condition.To having the Cu-Zn-Sn series copper alloy that the No.3 of sample shown in the table 9 forms, studied thermal treatment under the condition of different treatment temperature (specimen temperature) and temperature hold-time, the γ phase area occupation rate after the various thermal treatments.The speed of cooling of thermal treatment postcooling to 400 ℃, when treatment temp is in 425 ℃ or be 0.4～5K/ second when following, treatment temp is in 450 ℃ or be 5～10K/ second when following.

Table 10

Thermal treatment		γ phase area occupation rate (%)	The middle mutually Sn concentration (wt%) of γ
				Temperature (℃)	Time
400℃	30 seconds 1 minute 15 minutes 60 minutes					8 12 15 20	10.7 5.9 5.1 3.0
		425℃	30 seconds 1 minute 15 minutes 60 minutes	10 12 15 20	6.8 5.7 4.9 3.1
450℃	30 seconds 1 minute 15 minutes 60 minutes					10 12 15 15	9.7 9.1 8.2 8.5
		475℃	30 seconds 1 minute 15 minutes 60 minutes	8 8 8 10	10.3 10.5 11.3 7.0
500℃	30 seconds 1 minute 15 minutes 60 minutes					3 3 3 5	12.2 12.4 12.3 13.0
		550℃	30 seconds 1 minute 15 minutes 60 minutes	2 2 2 1	13.1 12.8 13.0 10.5

Table 10 explanation, if thermal treatment temp is in 550～400 ℃, soaking time reach 30 seconds or more than, and speed of cooling is in 5～10K/ scope second, then γ phase area occupation rate (%) be in 3.0% or more than.And in a single day thermal treatment temp be higher than 550 ℃, even soaking time prolongs γ phase area occupation rate increased, and the tendency that reduces is arranged on the contrary.So, want to make γ phase area occupation rate (%) reach 3% or more than, thermal treatment temp should be in 550 ℃ or following.And, in 400～450 ℃ of temperature ranges shown in the table 10, during thermal treatment, " α+γ type " crystal structure can be obtained, and in 450～550 ℃ of temperature ranges, during thermal treatment, " alpha+beta+γ type " crystal structure can be obtained.

Below just " tiny crystal grain " describe.In above-mentioned whole embodiment of brass of the present invention, average crystal grain diameter is in 15 μ m or following, preferred 10 μ m or following.Tiny like this crystal grain can forge under the temperature more much lower than the tradition product, and has high temperature ductility (ductility in the forging temperature district) and the quite high advantage of yield strength.

The miniaturization of crystal grain depends on the various conditions in the manufacturing process.For example, in the manufacturing process shown in the accompanying drawing 1, can select following condition in order to make tinyization of crystal grain.At first (step 1), the combined amount of regulating zinc are in the proper range α in the recrystallization temperature district mutually with β ratio mutually, promptly the ratio of β phase is in 30～80% scopes when mixing electrolytic copper, electrolytic zinc and cutting metal carry out melting and casting.β phase ratio is in the above-mentioned scope, is favourable (crystal grain diameter diminishes when producing dynamic recrystallization) for later on producing dynamic recrystallization when hot rolling and the high temperature forging.Then, be quenched to 400 ℃ or following with 5K/ second or above speed, molding in the middle of making in casting with in the process of cooling after solidifying.In this quenching process, crystal grain can tinyization.In addition, the setting rate after the casting is adjusted to 5 * 10～10 ⁵K/ second, preferred 10 ²～10 ⁵In K/ scope second, also be favourable for tinyization of crystal grain.

As other method that helps tinyization of cast sections crystal grain, it is effective adding elements such as B, Fe, Ni, P, Co, Nb, Ti, Zr in raw material.Its adding proportion (weight %) is: B0.005～0.5, Fe0.01～2.0, Ni0.05～0.2, P0.04～0.2, Co0.01～2.0, Nb0.01～0.2, Ti0.01～1.0, Zr0.005～0.5th, and suitable.Especially add P simultaneously with Fe, it is believed that to have collaborative effect this moment.

Then molding in the middle of this is heated in 480～650 (preferred 480～600) ℃ scope, hot rolling is configured as bar or material (step 2) under this temperature.In this extrusion process, make the section decrement reach 90% or the situation of above (preferably reaching more than 95%) under, be effective the lively attitude recrystallize of real estate, can prevent grain coarsening.In the process of cooling behind extrusion molding, be quenched to 400 ℃ or following, also can prevent the alligatoring of crystal grain with 0.4K/ second or above speed.In addition, the Heating temperature of molding in the middle of reducing, and shorten heat-up time, also be effective for the alligatoring that prevents crystal grain.

After this, this bar of cold letter or wire rod are annealed and pickling, cut into predetermined size, obtain forging with blank (step 3).The blank that heating obtains like this is so that guarantee to be suitable for the required characteristic of follow-up forging step.Heating temperature is in 480～750 ℃ of scopes, and utilizes the method that shortens heat-up time to keep tiny crystal grain.

And then heated blank placed forging mold, in 480～750 ℃ of scopes, carry out high temperature forging (step 5) under the temperature.Also be effective for the growth that suppresses coarse grain to keep the tiny degree of crystal grain, to shorten the being heated to forged time this moment.Cool off after the forging, for entering pickling and the step that sandblasts is prepared.Carry out the alligatoring of crystal grain behind the dynamic recrystallization when preventing high temperature forging, make speed of cooling be in 0.4K/ second or more than be favourable.

As mentioned above, in order to make speed of cooling and the extruding condition after grain refining should be noted that casting.At first utilize of the influence of accompanying drawing 12～15 detailed description speed of cooling to grain refining.

Accompanying drawing 12A is that expression will be cast the microphotograph that postcooling speed is decided to be the brass material crystal structure of making under the 19K/ condition of second.Accompanying drawing 12B is the moulded piece figure that makes of 12A with reference to the accompanying drawings.Accompanying drawing 13A is the microphotograph that the part of accompanying drawing 12B is amplified.Accompanying drawing 13B is the moulded piece figure that makes of 12A with reference to the accompanying drawings.In addition, accompanying drawing 14A is the microphotograph that the speed of cooling of expression after will casting is decided to be brass material crystal structure under the 1.3K/ situation of second.Accompanying drawing 14B is the moulded piece figure that makes of 14A with reference to the accompanying drawings.Accompanying drawing 15A is the microphotograph that the part of accompanying drawing 14A is amplified.Accompanying drawing 15B is the moulded piece figure that makes of 15A with reference to the accompanying drawings.

Illustrated as these accompanying drawings, in order to make the speed of cooling after the crystallization refinement should be accelerated to cast.For example, shown in accompanying drawing 13A and B, speed of cooling is decided to be under the 19K/ situation of second, average crystal grain diameter is 15 μ m or following, and almost in universe, all become α mutually with β blended tissue mutually.On the other hand, shown in accompanying drawing 15A and B, when speed of cooling being decided to be under the 1.3K/ situation of second, average crystal grain diameter be 15 μ m or more than, and γ separates out with β crystal boundary mutually mutually at α.Wherein, the mensuration of average crystal grain diameter is to carry out according to the standard of Japanese Industrial Standards (JIS).And, distinguish by further experiment, if average crystal grain diameter is in 15 μ m or following, speed of cooling must be decided to be 5K/ second or more than.

Below utilize of the influence of accompanying drawing 16～19 explanation extruding conditions to grain refining.

Accompanying drawing 16A is expression, 550 ℃ of extrusion temperatures, extrusion ratio 50%, the speed of cooling of extruding back forced air-cooling are under the condition such as 30K/ second, extruding Cu58.3 weight %, Sn1.9 weight %, surplus are the brass of Zn, the microphotograph of the bar-shaped extruding product crystal structure of making.Accompanying drawing 16B is the moulded piece figure that makes of 16A with reference to the accompanying drawings.Accompanying drawing 17A is expression, is shaped as cylindrically in forging, and compression method contracts with 1 axial compression, forging rate 50%, 550 ℃ of forging temperatures are forged under the condition such as postcooling speed 20K/ second, forge the microphotograph of the forged article crystal structure that the bar-shaped extruding product of accompanying drawing 16 expressions make.Accompanying drawing 17B is the moulded piece figure that makes of 17A with reference to the accompanying drawings.

Brass material shown in accompanying drawing 16A and the B, be α mutually and β mixing mutually, the β phase ratio during Forge Heating be in 30% or above and 80% or below, average crystal grain diameter is 15 μ m or following, belongs to " α+reinforcement β type " of the present invention.And shown in accompanying drawing 27A and B, after this brass material forges, crystal grain diameter, α mutually and β mutually ratio and the shape of crystal grain all not have variation.Do not produce in addition yet and forge fracture phenomena.

Accompanying drawing 18A is expression, 550 ℃ of extrusion temperatures, extrusion ratio 50%, the speed of cooling of extruding back forced air-cooling are under the condition such as 30K/ second, extruding has Cu58.7 weight %, Sn2.3 weight %, surplus is the brass that Zn forms, the crystal structure microphotograph of the bar-shaped extruding product of making.Accompanying drawing 18B is the moulded piece figure that makes of 18A with reference to the accompanying drawings.Accompanying drawing 19A is expression, is shaped as cylindrically in forging, and compression method contracts with 1 axial compression, forging rate 50%, 550 ℃ of forging temperatures are forged under the condition such as postcooling speed 20K/ second, forge the bar-shaped extruding product of accompanying drawing 18 expressions, the microphotograph of the forged article crystal structure of making.Accompanying drawing 19B is the moulded piece figure that makes of 19A with reference to the accompanying drawings.

Brass material shown in the accompanying drawing 18 also belongs to " α+reinforcement β type " of the present invention.Particularly the Sn content ratio of this material although forged disruptive 1 weight % above thinking in the past to produce significantly, does not still produce the forging fracture phenomena.Its reason causes owing to crystal grain diameter is tiny by inference.

The refinement of crystal grain is effective for obtaining good high-temperature ductility.And the crystal structure in the hot processing temperature district is α phase and β mixed phase mutually, so even β phase ratio is in 30～80% scopes, also can obtain high temperature ductility effectively.Its reason is as follows by inference.

When high temperature forging and hot rolling, in being subjected to the crystal boundary structure of external force, produce distortion.This is that atomic arrangement tanglewracks on the microcosmic, promptly produces dislocation.When producing dynamic recrystallization in the hot-work, because dislocation resets and can relax or eliminate distortion, so can obtain good ductility.Because of the energy of its dynamic recrystallization, be the heat energy of heating and the strain energy that external force produces.α is mutually and in the β mixed structure mutually, and the external force effect produces dislocation because of the stress of α phase particle firmly down in soft beta particle.When α mutually in crystal grain diameter when big, the distortion of (perhaps because big alpha-particle hinders the β crystal grain that produces dislocation to move) β in mutually is in concentration of local.On the other hand, under the tiny situation of the crystallization of α phase, the interior mutually distortion of (perhaps because the crystal boundary of α crystal grain and β intergranule produces slip, β crystal grain being moved) β disperses.For distortion concentrates on local and dispersive situation,, surpass this threshold value recrystallize and can obtain good high-temperature ductility because whole potential of distortion are big.

In addition, it is believed that adding Sn not only can improve the erosion resistance of β phase, but also can improve recrystallize speed.Improve recrystallize speed, with the ductility that improves under the effect of high speed external force.

And fully the processing back produces under the situation of recrystallize, and crystal grain reduces.If utilize the method that improves processing postcooling speed, prevent that dynamic recrystallization from forming the alligatoring of small grains, even also can obtain to keep the superperformance of small grains in the finished product then after processing.

Table 11 explanation and the present invention's the 4th type brass, under the normal temperature when final crystal structure, hot-work () the crystal structure optimum condition relevant with composition in recrystallization temperature the district in.The representative condition of high temperature extruding when the representative condition during the initial cast brass of table 12 explanation and this brass material of hot rolling obtain final composition the shown in the table 11.Table 13 illustrates high temperature extrusion brass material, and then obtains under the final composition situation extruding and forged representative condition through high temperature forging.Table 14 explanation is carried out the high temperature extruding with brass material, and then when doing high temperature forging and thermal treatment and finally being formed, about extruding, forging and heat treated representative condition.

Table 11

Type	Final crystal structure under the normal temperature	Crystal structure during hot-work	Form
					Apparent Zn content	Sn
			α + γ	α phase ratio: 97～76% (95～70) γ phase ratio: the mutually routine particle diameter of 3～30% (5～30) α: 15 μ m following (10 μ m are following) the mutually routine minor axis of γ: 8 μ m following (5 μ m are following) γ is mutually more than the middle Sn:8wt%			Alpha+beta 2 phase β phase ratios: 30～80% particle diameters: 15 μ m following (10 μ m are following)	37～46wt％ (38～46)	0.9～7wt％
α + β + γ	β phase ratio: 3～30% γ phase ratios: 3～30% α phases, β phase: 15 μ m following (10 μ m are following) α phase ratio: 40～94% γ phase minor axis: 8 μ m following (5 μ m are following) γ is mutually more than the middle Sn:8wt%
		α+conventional β	β phase ratio: (more than 25%) α phase, β phase more than 20%) particle diameter: 15 μ m following (10 μ m are following)	37～44wt％ (38～44)	0.5wt% less than
α+reinforcement β	β phase ratio: (more than 20%) α phase, β phase more than 15%) particle diameter: more than the middle mutually Sn:1.5wt% of 15 μ m following (10 μ m are following) β					0.5～7wt％

* in () preferred value

Table 12

Type	Method for making
				Casting	1. by hot-extrudable situation about finally being organized
	Hot-extrudable
			α + γ		Setting rate	5 * 10 1～10 5K/sec (10 2～10 5K/sec) speed of cooling to 400 of solidifying ℃ or when following be 5K/ second or more than	480～650 ℃ of (below 600 ℃) section decrements of temperature are more than 90% (more than 95%)	Speed of cooling to 400 ℃ is 0.4-5K/ second
α + β + γ	Speed of cooling to 400 ℃ is 0.4～10K/ second
		α+conventional β	Speed of cooling to 400 ℃ is that 0.4K/ is more than second
α+reinforcement β	Speed of cooling to 400 ℃ is 5～1000K/ second

Table 13

Type	Method for making
				2. by forging the situation about finally being organized of making
	Hot-extrudable	Forge
				α + γ	480～650 ℃ of (below 600 ℃) section slips of temperature (more than 95%) cooling velocity to 400 ℃ 0.4K/ more than second more than 90%	480～750 ℃ of temperature	Speed of cooling to 400 ℃ is 0.4～5K/ second
α + β + γ	Speed of cooling to 400 ℃ is 0.4～10K/ second
		α+conventional β	Speed of cooling to 400 ℃ is that 0.4K/ is more than second
α+reinforcement β	Speed of cooling to 400 ℃ is 5～1000K/ second

Table 14

Type	Method for making
				3. thermal treatment situation about finally being organized
	Hot-extrudable	Forge	Thermal treatment
				α + γ	480～650 ℃ of (below 600 ℃) section slips of temperature more than 90% (more than 95%) cooling velocity to 400 ℃ be that 0.4K/ is more than second	480～750 ℃ of speed of cooling 0.4K/ of temperature are more than second	400～550 ℃, 30 speed of cooling to 400 ℃ are 0.4～5K/ second
α + β + γ	450～550 ℃, 30 speed of cooling to 400 ℃ are 0.4～10K/ second
		α+conventional β	Not
α+reinforcement β	475～550 ℃, 30 speed of cooling to 400 ℃ are 5～1000K/ second

Below, with reference to table 11-14, the yellow crystal structure of the present invention, composition and typical method for making are described. (1) about the crystal structure under the normal temperature

" α+γ type " brass has α+γ crystal structure.α phase area ratio is 97～70%, and γ phase area ratio is 3～30%; Preferred α phase area ratio is 95～70%, and the area ratio of γ phase is 5～30%.α phase average particle diameter is 15 μ m or following, preferred 10 μ m or following; γ phase average particle diameter (being minor axis at this moment) is 8 μ m or following, preferred 5 μ m or following.According to microphotograph, on α phase crystal boundary, separate out γ phase thin layer (thickness 8 μ m or following).γ phase Sn concentration 8 weight % or more than, for example show among the embodiment 1～5 shown in 2A～2C, be 14～18%.

" alpha+beta+γ type " brass has alpha+beta+γ crystal structure.α phase area ratio is 40～94%, β mutually with γ mutually the area ratio of each phase be 3～30%.For example, among the embodiment 6～12 shown in table 2A～2C, α is 65～82.5% mutually, and β is 9.8～13.4% mutually, and γ is 4～24% mutually.α is 15 μ m or following with β median size mutually, preferred 10 μ m or following; γ phase average particle diameter (being minor axis at this moment) is 8 μ m or following, preferred 5 μ m or following.According to microphotograph, form the crystallization that γ phase thin layer (thickness 8 μ m or following) surrounds the β phase.γ phase Sn concentration is not less than 8 weight %, for example shows among the embodiment 6～12 shown in 2A～2C, and be 11～13.4%.

" α+conventional β type " brass is by having the alpha+beta crystal structure.β phase area ratio be 20% or more than, preferred 25% or more than, for example show among the embodiment 13～15 shown in 2A～2C, be 23.1～25.6%.α is 15 μ m or following with β median size mutually, preferred 10 μ m or following.

" α+reinforcement β type " brass has the alpha+beta crystal structure.β phase area ratio be 15% or more than, preferred 20% or more than, for example show among the embodiment 16～19 shown in 2A～2C, be 23～38%.α is 15 μ m or following with β median size mutually, preferred 10 μ m or following.β phase Sn concentration be 1.5 weight % or more than, for example show among the embodiment 16～19 shown in 2A～2C, be 2.5～7.1%.

(2) about hot worked (in the recrystallization temperature district) crystal structure

The brass of all types all has the alpha+beta crystal structure, and β phase area ratio is 30～80%.α is 15 μ m or following with β median size mutually, preferred 10 μ m or following.In fact α crystal grain exist with homodisperse form.

About forming (table 11)

In " α+γ type " and " alpha+beta+γ type " brass, apparent Zn content is 37～46 weight %, in order to obtain preferred 38～46 weight % of good hot rolling performance.All Sn content is 0.9～7 weight %.For example show among the embodiment 1～5 of " α+γ type " shown in 2A～2C, apparent Zn content is 37.8～44 weight %, and all Sn content is 1～5 weight %.In addition, among the embodiment 6～12 of " alpha+beta+γ type ", apparent Zn content is 41.5～44% weight, and all Sn content is 1.5～3.5% weight.

In " α+conventional β type " brass, apparent Zn content is 37～44 weight %, in order to obtain preferred 38～44 weight % of good hot rolling performance.For example show among the embodiment 13～15 shown in 2A～2C, apparent Zn content is 41.8～44 weight %.All Sn content is below the 0.5 weight %.

In " α+reinforcement β type " brass, apparent Zn content is 37～44 weight %, in order to obtain preferred 38～44 weight % of good hot rolling performance.All Sn content is 0.5～7 weight %.For example show shown in 2A～2C " embodiment 16～19 in, apparent Zn content is 40.1～42.6 weight %.All Sn content is 0.8～3.6 weight %.

(5) about casting condition (table 12)

Setting rate during casting is 5 * 10 ¹～10 ⁵K/ second, preferred value is 10 ²～10 ⁵K/ second.Not forming amorphous setting rate higher limit is 10 ⁵K/ second.Solidify postcooling to 400 ℃ or following speed of cooling and be 5K/ second or more than.

(6) obtain finally to organize hot-rolled condition under the situation about hot rolling

Hot-rolled temperature is 480～650 ℃, preferred 480～600 ℃.The section decrement be 90% or more than, preferred 95% or more than.Hot rolling postcooling to 400 ℃ or following speed of cooling for " α+γ type ", " alpha+beta+γ type " and " α+conventional β type ", are respectively: 0.4～5K/ second, 0.4～10K/ second and 0.4 ℃/second or more than; And " α+reinforcement β type " is 5～1000K/ second.For example, in the embodiment shown in table 2A～2C, speed of cooling when making " α+γ type " (embodiment 1～5), " alpha+beta+γ type " (embodiment 6～12) and " α+conventional β type " (embodiment 13～15) is 0.8K/ second (air cooling), and the speed of cooling when making " α+reinforcement β type " is 100K/ second (water-cooled).

(7) finally organized hot rolling and forge hot condition under the situation about high temperature forging

Speed of cooling after hot-rolled condition and the extruding is irrelevant, is the 0.4 above this point before being cooled to below 400 ℃, with top (6) middle illustrate identical.

Hot forging temperature is 480～750 ℃, is 500～600 ℃ in table 2A～2C illustrated embodiment for example.Forged Deformation velocity is more than 1/ second.Speed of cooling after the forging is with just the extruding back is described identical in top (6).

(8) finally organized hot rolling, forge hot and heat treated condition under the situation about thermal treatment (table 14)

Hot-rolled condition is identical with top (7) middle explanation.The forge hot condition is except speed of cooling (irrelevant with type) was cooled off this point with 0.4 above speed before being cooled to 400 ℃, with top (7) middle illustrate identical.

Do not need thermal treatment (that is, forge, can obtain the final composition of " α+conventional β type ") under the situation of manufacturing " α+conventional β type " brass according to above-mentioned condition.With regard to thermal treatment temp and soaking time, " α+γ type ", " alpha+beta+γ type " and " α+reinforcement β type " are respectively: 400～550 ℃ 30 seconds or more than, 450～550 ℃ 30 seconds or more than and 475～550 ℃ 30 seconds or more than.Speed of cooling after the thermal treatment is with identical with regard to what illustrate after the extruding in top (6).

Though more than just the representative instance of brass of the present invention and manufacture method thereof describe, its aim is to illustrate the present invention all the time, is not subjected to a bit restriction of these embodiment.Though the principle of the invention typically is applicable to brass, also can be applicable to brass alloy in addition.6, the possibility of utilizing on the industry

Alpha+beta+γ of the present invention, α+γ, α+conventional β and α+reinforcement β type brass, except can being used for valve uses among the purposes such as brass in the past with building materials, tame electrical articles etc. such as the first-class parts that contact with water of the fire hose, sanitary ware, various terminal, pipe, glass wares, door and handles, it is former thereby use the goods of material beyond the brass because of surface accuracy, erosion resistance, dimensional precision etc. to be used for the past.As using brass of the present invention, can list metal parts, water pipe, adapter and valve of usefulness such as hydrant, water-heater and warm water washing toilet seat or the like as the parts that contact with water.Several specific exampless below are described.

The water tap metalwork of brass of the present invention is used in accompanying drawing 20 expressions.By the withstand voltage little pipe connecting 23 of top hole pressure, rising pipe 25 is connected on the withstand voltage high body 21 of intake pressure.The minimum wall thickness (MINI W.) of body 21 is more than the 0.2mm, and the minimum wall thickness (MINI W.) of pipe connecting and rising pipe is 0.1mm.Accompanying drawing 21 is illustrated in other examples, uses the bend pipe of being made by forged article of the present invention 29 to link to each other with water pipe 27.In another example of accompanying drawing 22 expressions, will use the connection metalwork of making by forged article of the present invention 33 to receive shower nozzle with on the flexible pipe.In accompanying drawing 23 other examples of expression, the joint 41 between the pipe arrangement 35,37 and 39 can use brass forged article of the present invention.

Among accompanying drawing 24,25 and 26, the hot water machine parts that are to use brass of the present invention of expression.Accompanying drawing 24 is sectional drawings of expression hot water machine integral body.As shown in Figure 24, be connected the reducing valve on the water inlet pipe 51, be connected the induction pipe 55 that reducing valve 53 therewith links to each other on surplus valve 57, used brass of the present invention.Specifically, valve casing 61 in the reducing valve shown in the accompanying drawing 25 53 and valve handle 63 (dash area), and the valve body in the surplus valve shown in the accompanying drawing 26 57 71 (dash area) have all used brass of the present invention.

Because the erosion resistance of brass of the present invention and acid resistance are all good, so as above-mentioned during with parts that water contacts, the variation that the intensity of this contact wet part prolongs in time is little.In addition since brass of the present invention not only erosion resistance and acid-proof but also intensity are big, so can make thin with the wall thickness of water contact component.Specifically, in the JIS of water tap standard, the withstand voltage metal parts of the contact water of intake pressure is born in requirement, and withstand voltage properties reaches 17.5Kg/cm ²This withstand voltage properties requirement, must consider when determining the wall thickness of water contact component through the time corrosive nature wall thickness that causes reduce.In the past, for the cylindric water tap metal parts of 100mm, its minimum wall thickness was decided to be 1.0～1.5mm, and minimum wall thickness can be decided to be 0.8～1.2mm when using brass of the present invention in contrast to this.

In addition, because the machinability of brass of the present invention is good, so can shorten the machining time; And Yin Gaowen ductility is good, moves to left to forge to wait to add can be shaped at short notice man-hour.Because can forging and molding, so the degree of freedom of design also increases.High temperature ductility is good, and can be under 600 ℃ of following temperature cryogenic forging, so the precision of forged article and surface accuracy also improve, do not have oxide film in addition.

The purposes of alpha+beta+γ of the present invention, α+γ, α+conventional β and α+reinforcement β type brass is extremely wide, can be listed below, comprising the article that use brass in the past, use the article of other metals of stainless steel and so in the past, and the article that use non-metallic material in the past.

(1) starting material, intermediate, the finished product and molectron

The brass material of different shapes such as sheet material, tubing, bar, wire rod and bulk, intermediate, the finished product, its molectron, and with other materials bonded combination product.Utilize brass material that various working methods such as welding, melting welding, soldering, bonding, high-temperature machining, hot-work, forging, extruding, drawing, calendering, shearing, sheet material forming, rolling formation, rollforming, spinning, bending machining, shaping processing, high energy and high speed processing, powder processing, various machining and attrition process make, intermediate, the finished product, its molectron and with the combination product of other materials combination.Through metal film coated processing, change into that processings, surface hardening are handled, nonmetal overlay film is handled and brass material, intermediate, the finished product, its molectron that various surface treatments such as application are made and the combination product that makes up with other materials.

(2) Transport Machinery parts

(2-1) be used for the parts of automobile and cart

Drive disk assembly, for example synchromesh gear, bearing etc.Engine parts, for example timing gear, pulley, bearing, shaft coupling, fuel distribution tube, vapor pipe, seal washer, nozzle, power pack etc.Scatterer, for example tube stub.Car body.Extraneous adornment product, for example moulded piece, door handle and wiper etc.Internal part, for example instrument, warning howler etc.Drive based part, for example take turns that nausea is chewed, axletree, wheel shaft etc.Brake parts, for example shaft coupling etc.Steering parts, for example shaft coupling, gear etc.Air conditioning machinery parts, for example tube stub etc.Suspension systems components, for example bearing etc.Oil-pressure pump parts, for example pump housing, valve, piston etc.

(2-2) small-sized and large ship parts

Engine parts, for example timing gear, pulley, bearing, shaft coupling, fuel distribution tube, vapor pipe, seal washer, nozzle, power pack etc.Hull.Boat-carrying parts, for example place railing, moulded piece, door handle, mast etc.Drive based part, for example water screw, thruster, axle etc.Measuring instrument parts, for example housing, handle etc.The steering parts.The air conditioning machinery parts.Oil-pressure pump parts etc.

(2-3) rail truck parts

Engine parts, for example timing gear, pulley, bearing, shaft coupling, fuel distribution tube, vapor pipe, seal washer, nozzle, power pack etc.Motor component, for example housing, bearing, cooling tube joint etc.Drive disk assembly, for example synchromesh gear, bearing etc.Scatterer, for example tube stub.Car body.Extraneous adornment product, for example moulded piece, door handle and wiper etc.Inside components, for example instrument, warning howler, handrail etc.Drive based part, for example take turns that nausea is chewed, axletree, wheel shaft etc.Brake parts, for example shaft coupling etc.Steering parts, for example oil-pressure pipe joint, gear, handle etc.Air conditioning machinery parts, for example tube stub etc.Suspension systems components, for example bearing etc.Oil-pressure pump parts, for example pump housing, valve, piston etc.Pantograph parts, for example shaft coupling etc.Stringing parts, for example tube stub etc.

(2-4) aircraft, spaceship, elevator, recreation are taken and are used parts

(3) industrial machine parts

(3-1) construction Machines parts

Engine parts, for example timing gear, pulley, bearing, shaft coupling, fuel distribution tube, vapor pipe, seal washer, nozzle, power pack etc.Motor component, for example housing, bearing, cooling tube joint etc.Drive disk assembly, for example synchromesh gear, bearing etc.Heat sink assembly, for example tube stub.Extraneous adornment parts, for example moulded piece, door handle and wiper etc.Inside components, for example instrument, warning howler, handrail etc.Brake parts, for example shaft coupling etc.Steering parts, for example oil-pressure pipe joint, gear, handle etc.Air conditioning machinery parts, for example tube stub etc.Suspension systems components, for example bearing etc.Oil-pressure pump parts, for example pump housing, valve, piston etc.

(3-2) welding machine parts

Gas welding machine parts, for example welding gun etc.Arc welding machine parts, for example welding gun etc.Plasma welding is met sb. at the airport and is used parts, for example welding gun etc.

(3-3) metal die and parts thereof

(3-4) roller path parts

(3-5) bearing, gear

(3-6) parts that machinery slides such as connect synchronously

(3-7) heat exchanger parts

Boiler component, for example body of heater, valve etc.Solar water heater parts, for example body, valve etc.

(4) musical instrument part

(4-1) keyboard instrument part piano part, for example pedal, shaft coupling etc.Electric organ part, for example pedal, shaft coupling etc.Organ part, for example pedal, shaft coupling, resonating tube etc.

(4-2) wind instrument part

Small size part, for example body, piston, lever, shaft coupling etc.Trombone part, for example body, piston, lever, shaft coupling etc.Brass bugle part, for example body, piston, lever, shaft coupling etc.Clarinet part, for example piston, lever, shaft coupling etc.Bassoon part, for example piston, lever, shaft coupling etc.

(4-3) percussion instrument part

Drum part, for example support, big cymbals etc.Big drum part, for example support, bronze drum parts etc.Xylophone part, for example resonating tube, support etc.

(5) electrical apparatus product parts

(5-1) audio-visual appliances parts

The parts of amplifier, vide player, cassette tape player, CD player and LD player, for example adjusting knob, bearing, loudspeaker cone etc.

(5-2) gas, liquid control machine parts

Indoor air conditioner parts, for example tube stub, heat-eliminating medium pipe, valve etc.Hot water machine and electric water heater parts, for example housing, hot water storing containers, gas pipe arrangement, gas jet, burner, reducing valve, surplus valve, proportional valve, magnetic valve, pump parts etc.Household heater and room cooler parts, for example gasifier, heat-eliminating medium pipe, make-up valve, oil pipe nut etc.

(5-3) tame electrical article parts

Part of washing machine, for example washing composition casing, rinse bath etc.

(5-4) sewing machine, braiding machine parts

(5-5) recreation product parts

The pachinko parts.The vending machine parts.

(5-6) outdoor electrical apparatus product parts

Vending machine parts, for example coin slot, Coin acceptor etc.

(5-7) electrical equipment, electronic circuit parts

Control basal plate, printed circuit board (PCB), switchboard electrode, switch part, resistor part, attaching plug part, lamp socket, lamp socket part, discharge electrode, water logging electrode, copper cash, battery terminal, housing and solder etc.

(6) dwelling house articles for use

(6-1) building materials

Exterior decoration building materials, building material made, wall dunnage, reinforcing bar, steelframe etc.

(6-2) furring product

Door part, for example door wall dunnage, handle, pile, moulded piece, hinge etc.Door part, for example door pillar, door leaf, moulded piece, hinge etc.Fence parts, for example fence body, moulded piece etc.Outdoor lamp part, for example lamp housing, lampshade, lamppost etc.Window shutter, the balcony fence is posted bucket, rainwater pipe, drain tub, roof, automatic water sprayer, metal hose.

(6-3) interior decoration product

Armrest member, for example handrail tube, tube stub etc.Door part, for example handle, pile, moulded piece, hinge etc.Kitchen tackle, for example gas range burner, operator's console panel etc.Bathhouse article, for example admission port orifice plate, water discharge valve, draining valve ball chain, watering plate etc.Washroom articles for use, for example metal parts of fixed mesa, towel bar etc.Room articles for use, for example chandelier parts, illuminace component, decoration etc.Lavatory articles for use, for example wall dunnage of outer wall etc. between the lavatory.Furniture parts, for example setting nut of chair angle, desk angle, desktop, hinge, handle, guide rail, shelf etc.

(6-3) sacrificial place, niche for a statue of Buddha articles for use

Handrail members, for example handrail tube, pipe connecting etc.Niche for a statue of Buddha parts, for example figure of buddha, moulded piece, candlestick, clock etc.

(7) precision instrument part

(7-1) opticinstrument and mensuration, surveying instrument part

The part of photographic camera, visual telescope, microscope and electron microscope, for example matrix, support, camera lens shell etc.

(7-2) timepiece

The parts of wrist-watch, wall clock and desk clock, for example clock body, pointer, moulded piece, gear, pendulum etc.

(8) writing appliance and office appliance

Writing utensil equipped, for example ballpoint pen, pencil-knife etc.Scissors, paper cutter, front cover, folder, drawing pin, steel tape, ruler, キ ヤ PVC ネ Star プ, template, magnet, bookshelf, telephone frame parts, book-end, tapping and plugging machine part, stapler part, pencil cutting machine part and cabinet etc.

(9) supplying drainage, valve and water tap articles for use

Drain plug, polyvinyl chloride hard Pipe joint, draining are enough, bend pipe, tube stub, hose nipple with corrugated tube, plumbing piston, valve, closet with joint flange, axostylus axostyle, main shaft, ball valve, ball, valve cup ring, sealing nut, KCP connecting leg, water tank, shunting bolt, flexible pipe, hose nipple, water bolt body, water bolt metalwork, valve body, ball float plug, stopcock, single function water bolt, the moving water bolt of heat, two valve wall water bolts, two valve seat water bolts, spout, UB bend pipe, mixing valve etc.

(10) ornament, furnishings

Ear nail, earrings, ring, safety pin, famous brand, tiepin, イ パ-, bracelet, robe with metalwork, footwear with metalwork, clothes with ornament and furnishingss such as metalwork, button, fastener, hook spare, belt metalworks.

(11) sporting goods, weapon

Golf club's articles for use, for example long handle of golf club, bar head, ト ウ, ヒ-Le, ソ-Le etc.Dumbbell, barbell, speedboat skeleton, horse-vaulting device frame, block, ground, sword-play place, skates, ski, ski frenulum, diving articles for use, gymnastics equipment, bike blockchain, tent holding appliance, pistol part, rifle part, firelock part, daggers and swords part, bullet etc.

(12) jar, container

The jar and the container of splendid attire food, beverage, fuel, coating, powder, liquids and gases etc.

(13) medical apparatus

Bedstead, scalpel, endoscope part, dental instrument part, diagnosis utensil part, surgical instrument part, therapeutic appliance part etc.

(14) instrument, farm implements and building apparatus

Pliers, hammer, ruler, awl, file, saw, nail, chisel, plane, drill bit, fixer, anchor clamps, grinding stone frame, screw, bolt, nut, screw, spade, axe, scoop etc.

(15) cooker, small stores

Pot, still, kitchen knife, round-bottomed frying pan, spoon, spoon, fork, knife, tin-opener, cork, Off ラ イ return, fried prawn is used chopsticks, hot plate, bamboo strainer, pot-scouring brush, wastepaper basket, rubbish container, portable tube, washbowl, watering can etc.

(16) groceries, horticultural apparatus, small article

Teacup, replica, lighter, candlestick, character goods, medal, bell, hair clip, the apparatus of haircuting, ashtray, vase, key, coin, fishing tackle, false bait, eyes frame, nail clipper, pachinko ball, worm cage, umbrella, Jian Shan, pin, pruning scissors, gardening pillar, gardening support, gardening canopy, flowerpot, fingerstall, lantern, strong box, roller etc.

Claims (32)

1. brass, apparent Zn content is 37～46 weight %, has the alpha+beta crystal structure in the recrystallization temperature district, the crystal structure in this recrystallization temperature district satisfies following full terms:

(A1) β phase area ratio is 30～80%,

(A2) α mutually with above-mentioned β average crystal grain diameter mutually below 15 μ m, and

(A3) above-mentioned α disperses to exist mutually.

2. the manufacture method of a brass, comprising: cast the step of making brassing under the following conditions and above-mentioned brassing be heated to step till the recrystallization temperature:

(1) the apparent Zn content of raw material composition is 37～46 weight %,

Setting rate when (2) casting is 5 * 10 ¹～10 ⁵K/ second, and

(3) speed of cooling after solidifying: be cooled to below 400 ℃ with the speed of 5K/ more than second.

3. the manufacture method of a brass, this method has the brass material that hot-extrudable apparent Zn content is 37～46 weight % under following condition and makes the step that brass is extruded part, temperature when (1) extruding is in 480～650 ℃ of temperature ranges, and the section decrement is more than 90% when (2) extruding, and is preferred more than 95%.

4. the manufacture method of a brass, comprising the step that with apparent Zn content is the brass material heating postcooling of 37～46 weight %, with control Heating temperature for the cooled crystal structure of above-mentioned brass material can be selected in α+γ, alpha+beta and alpha+beta+γ, the step of heating one of hold-time and speed of cooling.

5. a brass is characterized in that apparent Zn content is 37～46 weight %, has α+γ crystal structure under the normal temperature, and the crystal structure under this normal temperature satisfies following full terms:

(1) γ phase area ratio is 3～30%,

(2) α phase average crystal grain diameter is below the 15 μ m,

(3) above-mentioned γ phase average crystal grain diameter (minor axis) is below the 8 μ m,

(4) on above-mentioned α phase crystal boundary, there is above-mentioned γ phase, and

(5) the middle mutually Sn concentration of above-mentioned γ is more than the 8 weight %.

6. a brass is characterized in that apparent Zn content is 37～46 weight %, has alpha+beta+γ crystal structure under the normal temperature, and the crystal structure under this normal temperature satisfies following full terms:

(1) β is more than 3% with γ area ratio mutually mutually,

(2) α is mutually with below β average crystal grain diameter mutually is 15 μ m,

(3) above-mentioned γ phase average crystal grain minor axis is below the 8 μ m,

(4) above-mentioned γ surrounds above-mentioned β phase mutually, and

(5) the middle mutually Sn concentration of above-mentioned γ is more than the 8 weight %.

7. a brass is characterized in that apparent Zn content is 37～46 weight %, has the alpha+beta crystal structure under the normal temperature, and the crystal structure under this normal temperature satisfies following full terms:

(1) β phase area ratio is more than 20%, and

(2) α is mutually with below above-mentioned β average crystal grain diameter mutually is 15 μ m.

8. a brass is characterized in that apparent Zn content is 37～46 weight %, has the alpha+beta crystal structure under the normal temperature, and the crystal structure under this normal temperature satisfies following full terms:

(1) β phase area ratio is more than 15%,

(2) α is mutually with below above-mentioned β average crystal grain diameter mutually is 15 μ m, and

(3) the middle mutually Sn concentration of above-mentioned β is more than the 1.5 weight %.

9. the manufacture method of a brass, it is characterized in that having and cast the step of making brassing under the following conditions: the apparent Zn content that (1) raw material is formed is 37～46 weight %, the setting rate during (2) casting is 5 * 10 ¹～10 ⁵K/ second, and (3) speed of cooling after solidifying: be cooled to below 400 ℃ with the speed of 5K/ more than second.

10. the manufacture method of a brass, it is that 0.5～7 weight % and apparent Zn content are that the brass material of 37～46 weight % is made the step that brass is extruded part that this method has under following condition hot-extrudable Sn concentration, temperature when (1) extruding is 480～650 ℃, and (2) when extruding the section decrement be more than 90%.

11. the producing apparatus of a brass, cast comprising can or being adjusted under the following condition its structure design, make the casting device of brassing: the raw material that (1) can add apparent Zn content is 37～46 weight %, the setting rate during (2) casting is 5 * 10 ¹～10 ⁵K/ second, and (3) speed of cooling after solidifying: be cooled to below 400 ℃ with the speed that is higher than 5K/ second.

12. the producing apparatus of a brass, this equipment has can accept the brass starting material that apparent Zn content is 37～46 weight %, and hot-extrudable manufacturing brass is extruded the device of part under following condition, temperature when (1) extruding is 480～650 ℃, and (2) when extruding the section decrement be more than 90%.

13. the producing apparatus of a brass, comprising adding the brass raw material that apparent Zn content is 37～46 weight %, heat above-mentioned brass material, under 480～750 ℃ of temperature, carry out high temperature forging, make the forging apparatus of brass forging, said high temperature forging Deformation velocity is more than 1/ second.

14. brass producing apparatus, wherein can add the brass raw material that apparent Zn content is 37～46 weight %, mechanism with the above-mentioned brass material postcooling of heating, can be to the Heating temperature of said mechanism, one of heating hold-time and speed of cooling are adjusted, make above-mentioned brass starting material cooling post crystallization tissue, have any structure among α+γ, alpha+beta and the alpha+beta+γ.

15. the manufacture method of a brass, this method comprises the step with the brass material heating postcooling of apparent Zn content 37～46 weight %, as the speed of cooling in the above-mentioned cooling, first speed of cooling that makes the cooled crystal structure of above-mentioned brass material become α+γ is arranged, become second speed of cooling of alpha+beta and become at least 2 speed of cooling that may select in the 3rd speed of cooling of alpha+beta+γ, from these two speed of cooling that may select, select the step of one.

16. a brass is forged the manufacture method of forging piece, this method comprises:

With apparent Zn content is 37～46 weight %, and to have in recrystallization temperature district β phase area ratio be 30～80% crystal structure brass material, in the step of above-mentioned recrystallization temperature district internal heating, and

In above-mentioned recrystallization temperature district, said brass material is forged the step of making brass forging.

17, a kind of manufacture method that is used for forged brass material, this method comprises:

The raw material that to use apparent Zn content be 37～46 weight % forges, make brass material step and

Setting rate when above-mentioned forging is carried out in control and solidify after speed of cooling, make the step of the crystal grain diameter refinement of above-mentioned brass material,

So that thus when above-mentioned brass material being heated to recrystallization temperature for forging, make the crystal structure of above-mentioned brass material contain at least α mutually and β mutually, and the α phase is in 15 μ m or following with β average crystal grain diameter mutually.

18, a kind of manufacture method that is used for forged brass material, this method comprises:

The raw material that to use apparent Zn content be 37～46 weight % forges, make brass material step and

Setting rate when above-mentioned forging is carried out in control and solidify after speed of cooling, make the step of the crystal grain diameter refinement of above-mentioned brass material, and

So that thus when above-mentioned brass material being heated to recrystallization temperature for forging, make the crystal structure of above-mentioned brass material contain at least α mutually and β mutually, and make at least one condition in satisfied at least (a)～(d) condition of above-mentioned brass foundry part:

It is not (a) damaged when producing 100% distortion under the Deformation velocity in 1/ second,

It is not (b) damaged when producing 200% distortion under the Deformation velocity in 0.1/ second,

Not damaged when (c) producing under the Deformation velocity at 0.01/ second greater than 200% distortion, or

Not damaged when (d) producing under the Deformation velocity at 0.001/ second greater than 600% distortion.

19, a kind of manufacture method of brass rod, this method comprises:

Using apparent Zn content is that the brass raw material of 37～46 weight % carries out hot rolling, make brass rod step and

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or following step,

So that behind above-mentioned cooling step, make the average crystal grain diameter of above-mentioned brass rod be in 15 μ m or following.

20, a kind of manufacture method of brass rod, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, make above-mentioned brass rod grain refining step and

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or following step,

Make thus behind above-mentioned cooling step, above-mentioned brass rod has following characteristic: with the round brass rod of cutting soon that meets the JIS C-3604 of Japanese Industrial Standards regulation is that benchmark cutting resistance coefficient is not less than 80, and 0.2% yield strength or yielding stress are not less than 300N/mm ²

21, a kind of manufacture method of brass rod, comprising:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, make above-mentioned brass rod grain refining step and

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or following step,

Make thus behind above-mentioned cooling step, above-mentioned brass rod has following SCC resistance: the following cylindrical sample with above-mentioned brass rod of loading exposes 24 hours in the ammonia atmosphere gas above 14% ammonia soln after, said sample not disruptive maximum stress is 180N/mm ²Or more than.

22, a kind of manufacture method of brass rod, this method comprises:

It is hot-extrudable to use apparent Zn content to be that 37～46 weight % and Sn concentration are that the brass raw material of 0.5～7 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, make above-mentioned brass rod grain refining step and

Carry out above-mentioned hot-extrudable after, on one side above-mentioned brass rod is cooled to 400 ℃ or following, controlled chilling speed on one side so that the cooling step of the Sn concentration in the crystallization control,

Make thus that behind above-mentioned cooling step the cutting resistance coefficient of above-mentioned brass rod is not less than 80 to meet cutting soon under the situation that round brass rod is a benchmark of the JIS C-3604 of Japanese Industrial Standards; And have at least satisfy following (a) and (b) in the erosion resistance of one of condition: stretch the technological standard JBMA T-303 of copper association according to Japan and carry out Dezincification corrosion when testing, (a) under the maximum dezincify depth of penetration direction situation parallel with machine direction, the maximum dezincify degree of depth is 100 μ m or following; And (b) under maximum dezincify depth of penetration direction and the vertical situation of machine direction, the maximum dezincify degree of depth is 70 μ m or following.

23, the manufacture method of the forged brass material of a kind of usefulness, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, make above-mentioned brass material the crystal grain diameter refinement step and

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or following step,

Make thus for forging when above-mentioned brass rod is heated to recrystallization temperature, contain at least in the crystal structure of above-mentioned brass material α mutually with β mutually, and the average crystal grain diameter of α phase is in 15 μ m or following.

24, a kind of manufacture method that is used for forged brass material, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, make above-mentioned brass material the crystal grain diameter refinement step and

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or following step,

Make thus for forging when above-mentioned brass rod is heated to recrystallization temperature, contain at least in the crystal structure of above-mentioned brass material α mutually and β mutually, and satisfied at least (a)～(d) one of condition:

It is not (a) damaged when producing 100% distortion under the Deformation velocity in 1/ second,

It is not (b) damaged when producing 200% distortion under the Deformation velocity in 0.1/ second,

Not damaged when (c) producing under the Deformation velocity at 0.01/ second greater than 200% distortion, or

Not damaged when (d) producing under the Deformation velocity at 0.001/ second greater than 600% distortion.

25, a kind of manufacture method of brass forging, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, makes the step of the grain refining of above-mentioned brass rod,

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or the first following cooling step,

Behind above-mentioned first cooling step, above-mentioned brass rod reheat forged to recrystallization temperature makes, make brass forge forging piece step and

After carrying out above-mentioned forging, above-mentioned brass forging is cooled to 400 ℃ or the second following cooling step,

Make that thus after above-mentioned second cooling step, the average crystal grain diameter of above-mentioned brass forging is not more than 15 μ m.

26, a kind of manufacture method of brass forging, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, makes the step of the grain refining of above-mentioned brass rod,

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or the first following cooling step,

Behind above-mentioned first cooling step, above-mentioned brass rod reheat is forged under recrystallization temperature, make brass forging step and

After carrying out above-mentioned forging, above-mentioned brass forging is cooled to 400 ℃ or the second following cooling step,

Make thus after above-mentioned second cooling step, above-mentioned brass forging has following characteristic: with the round brass rod of cutting soon that meets the JIS C-3604 of Japanese Industrial Standards regulation is that the cutting resistance coefficient of benchmark is not less than 80, and 0.2% yield strength or yielding stress are 300N/mm ²Or more than.

27, a kind of manufacture method of brass forging, this method comprises:

It is hot-extrudable to use apparent Zn content to be that the brass raw material of 37～46 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, makes the step of the grain refining of above-mentioned brass rod,

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or the first following cooling step,

Behind above-mentioned first cooling step, above-mentioned brass rod reheat is forged under recrystallization temperature, make brass forging step and

After carrying out above-mentioned forging, above-mentioned brass forging is cooled to 400 ℃ or the second following cooling step,

Make thus after above-mentioned second cooling step, above-mentioned brass forging has following SCC resistance: with after exposing 24 hours in the ammonia atmosphere gas of cylindrical sample above 14% ammonia soln of above-mentioned brass rod, said sample not disruptive maximum stress is not less than 180N/mm under loading ²

28, a kind of manufacture method of brass forging, this method comprises:

It is hot-extrudable to use apparent Zn content to be that 37～46 weight % and Sn concentration are that the brass raw material of 0.5～7 weight % carries out, and makes the step of brass rod,

Above-mentioned temperature and section decrement when hot-extrudable carried out in control, makes the step of the grain refining of above-mentioned brass rod,

Carry out above-mentioned hot-extrudable after, above-mentioned brass rod is cooled to 400 ℃ or the first following cooling step,

Behind above-mentioned first cooling step, above-mentioned brass rod reheat is forged under recrystallization temperature, make brass forging step and

After carrying out above-mentioned forging, utilize above-mentioned brass forging limit is cooled to 400 ℃ or with the method for following controlled chilling speed, control second cooling step of Sn concentration in the above-mentioned brass forging,

Make thus that after above-mentioned second cooling step cutting resistance coefficient value of above-mentioned brass forging meets cutting soon under the situation of round brass rod as benchmark of the JIS C-3604 of Japanese Industrial Standards and is not less than 80 using; And have at least satisfy following (a) and (b) in the erosion resistance of one of condition: stretch the technological standard JBMA T-303 of copper association according to Japan and carry out Dezincification corrosion when testing, (a) under the maximum dezincify depth of penetration direction situation parallel with machine direction, the maximum dezincify degree of depth is 100 μ m or following; (b) under maximum dezincify depth of penetration direction and the vertical situation of machine direction, the maximum dezincify degree of depth is 70 μ m or following.

29, a kind of manufacture method of brass material, this method comprises:

Using apparent Zn content is that the brass raw material of 37～46 weight % is cast, make brass material step and

Setting rate when above-mentioned casting is carried out in control and solidify after speed of cooling, make the step of the crystal grain diameter refinement of above-mentioned brass material,

So that make the average crystal grain diameter of above-mentioned brass material be in 15 μ m or following.

30, a kind of manufacture method of brass material, this method comprises:

Using apparent Zn content is that the brass raw material of 37～46 weight % is cast, make brass material step and

Setting rate when above-mentioned casting is carried out in control and solidify after speed of cooling, make the step of the crystal grain diameter refinement of above-mentioned brass material,

So that make above-mentioned brass material have following characteristic: with the round brass rod of cutting soon that meets the JIS C-3604 of Japanese Industrial Standards regulation is benchmark, and its cutting resistance coefficient is not less than 80, and 0.2% yield strength or yielding stress are not less than 300N/mm ²

31, a kind of manufacture method of brass material, this method comprises:

Using apparent Zn content is that the brass raw material of 37～46 weight % is cast, make brass material step and

Setting rate when above-mentioned casting is carried out in control and solidify after speed of cooling, make the step of the crystal grain diameter refinement of above-mentioned brass material,

So that make above-mentioned brass material have following SCC resistance: with after exposing 24 hours in the ammonia atmosphere gas of cylindrical sample above 14% ammonia soln of above-mentioned brass material, said sample not disruptive maximum stress is not less than 180N/mm under loading ²

32, a kind of manufacture method of brass material, this method comprises:

Using apparent Zn content is 37～46 weight %, and Sn concentration is that the brass raw material of 0.5～7 weight % is cast, make brass material step and

Setting rate when above-mentioned casting is carried out in control and solidify after speed of cooling, make the step of Sn concentration in the crystal grain diameter refinement of above-mentioned brass material and the crystallization control,

So that make the cutting resistance coefficient value of above-mentioned brass material, meet cutting soon under the situation of round brass rod as benchmark of the JIS C-3604 of Japanese Industrial Standards and be not less than 80 using; And have at least and to satisfy following (a) and (b) erosion resistance of one of condition: stretch the technological standard JBMAT-303 of copper association according to Japan and carry out Dezincification corrosion when testing, (a) under the maximum dezincify depth of penetration direction situation parallel with machine direction, the maximum dezincify degree of depth is not more than 100 μ m; (b) under maximum dezincify depth of penetration direction and the vertical situation of machine direction, the maximum dezincify degree of depth does not lie in 70 μ m.

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