Low thermal expansion alloy

Abstract

Provided is a low thermal expansion alloy wherein martensitic transformation does not occur even at −120° C. This low thermal expansion alloy contains, in mass %, 1.50-5.00% of Co, while containing Ni in such an amount that if [Ni] (mass %) is the content of Ni and [Co] (mass %) is the content of Co, [Co]≥−4×[Ni]+136 and [Co]≤−4×[Ni]+139 are satisfied, with the balance being made up of Fe and unavoidable impurities. This low thermal expansion alloy has an average thermal expansion coefficient of 0.5×10.sup.−6/° C. or less for the range of 0-30° C., while having a martensitic transformation temperature of −120° C. or less.

Claims

1. A low thermal expansion alloy consisting of, by mass %, Co: 1.50 to 5.00%, Ni satisfying
[Co]≥−4×[Ni]+136 and
[Co]≤−4×[Ni]+139 wherein [Ni] (mass %) is a content of Ni and [Co] (mass %) is a content of Co, and a balance of Fe and unavoidable impurities, wherein a mean thermal expansion coefficient at 0 to 30° C. is 0.5×10.sup.−6/° C. or less and a martensite transformation temperature is −120° C. or less.

2. A low thermal expansion alloy, consisting of, by mass %, Co: 1.50 to 5.00%, Ni satisfying
[Co]≥−4×[Ni]+136 and
[Co]≤−4×[Ni]+139 wherein [Ni] (mass %) is a content of Ni and [Co] (mass %) is a content of Co, and one or more of: C: 0 to 0.040%, Si: 0 to 0.30%, Al: 0 to 0.20%, Mg: 0 to 0.100%, Ca: 0 to 0.100%, Ce: 0 to 0.100%, and La: 0 to 0.100%, and a balance of Fe and unavoidable impurities, wherein: a mean thermal expansion coefficient at 0 to 30° C. is 0.5×10.sup.−6/° C. or less and a martensite transformation temperature is −120° C. or less.

3. The low thermal expansion alloy according to claim 1, wherein the mean thermal expansion coefficient at 0 to 30° C. is −0.04×10.sup.−6/° C. or less.

Description

DESCRIPTION OF EMBODIMENTS

(1) Below, the present invention will be explained in detail. Below, the “%” relating to the chemical composition will mean “mass %” unless indicated otherwise. First, the chemical composition of the low thermal expansion alloy of the present invention will be explained.

(2) Co is an essential element for lowering the thermal expansion coefficient. To make the thermal expansion coefficient a desired range, the content of Co is made 1.50 to 5.00%. To obtain a lower thermal expansion coefficient, preferably the content is made 2.50 to 4.50%.

(3) The low thermal expansion alloy of the present invention may further contain the following constituents. The elements other than Co are not essential. The contents may also be 0.

(4) C forms a solid solution in austenite and contributes to improvement of the strength. If the content of C becomes greater, the thermal expansion coefficient becomes larger. Furthermore, the ductility falls and casting cracks easily occur, so the content is made 0.040% or less, preferably 0.010% or less.

(5) Si is added as a deoxidizer. If the amount of Si exceeds 0.30%, the thermal expansion coefficient increases, so the amount of Si is made 0.30% or less, preferably 0.10% or less. To improve the fluidity of the melt at the time of casting, Si is preferably included in 0.05% or more.

(6) Mn is added as a deoxidizer. Further, it also contributes to improvement of strength by solid solution strengthening. If the content of Mn is too great, the thermal expansion coefficient becomes higher, so the amount of Mn is 0.50% or less, preferably 0.20% or less.

(7) Ni is an essential element for lowering the thermal expansion coefficient. In the low temperature stability type low thermal expansion alloy of the present invention, to lower the martensite transformation temperature and obtain a stable microstructure with stable austenitic structure even at −120° C., the balance of the amount of Ni and the amount of Co is important. Specifically, when [Ni] (mass %) is a content of Ni and [Co] (mass %) is a content of Co, it is necessary to include Ni satisfying [Co]≥−4×[Ni]+136 and [Co]≤−4×[Ni]+139. For example, when the amount of Co is 3.00%, the content of Ni is made 33.25 to 34.00%. By limiting Ni to a restricted range in this way, it is possible to obtain a microstructure stable at low temperature. To obtain a lower thermal expansion coefficient, preferably [Co]≥−4×[Ni]+136, and [Co]≤−4×[Ni]+138.

(8) Al is added for the purpose of deoxidation. Further, to keep inclusions from forming, reduce casting defects, and obtain a further lower thermal expansion coefficient, the content is made 0 to 0.20%.

(9) Mg bonds with S contained as an impurity and thereby has the function of keeping down grain boundary segregation of S and improving the hot ductility. The content of Mg is made 0 to 0.100%.

(10) Ca bonds with S to form sulfides and is useful for improving the hot workability and improving the ductility at ordinary temperature. The content of Ca is made 0 to 0.100%.

(11) Ce and La are elements suppressing a drop in ductility due to sulfides. The contents of Ce and La are respectively made 0 to 0.100%.

(12) The balance of the chemical composition is comprised of Fe and unavoidable impurities. The “unavoidable impurities” are constituents which unavoidably enter from the raw materials, manufacturing environment, etc. when industrially manufacturing steel having the chemical composition prescribed in the present invention.

(13) By producing an alloy having the above chemical composition by casting, it is possible to obtain a low thermal expansion alloy with stable austenitic structure even at a low temperature. The mold used when producing low thermal expansion alloy of the present invention, the apparatus for pouring the molten steel into the mold, and the pouring method are not particularly limited. Known apparatuses and methods may be used. It is possible to work the produced cast alloy by direct machining etc. or work it after forging to obtain a steel part.

(14) The low temperature stability of the low thermal expansion alloy of the present invention can be confirmed by holding the alloy in a low temperature atmosphere and examining for any martensite transformed structures. For example, it is possible to use the method of using liquid nitrogen to hold a test piece in a −120° C. atmosphere for 15 minutes, then use an optical microscope to examine for any martensite transformed structures.

(15) Furthermore, to lower the thermal expansion coefficient more, diffusion treatment or solid solution treatment may also be performed. The diffusion treatment is performed after casting in the case of a casting and before heating for forging or at an intermediate stage of forging in the case of a forging. The solid solution treatment is performed before working, that is, directly after casting or after casting and forging. The diffusion treatment holds a casting at 1100 to 1300° C. for 10 to 50 hr then air cools or furnace cools it. The solid solution treatment heats the alloy to preferably 600 to 1000° C., more preferably 650 to 850° C., holds it there for 0.5 to 5 hr, then rapidly cools it. The cooling rate is preferably 10° C./min or more, more preferably 100° C./min or more. Due to the solid solution treatment, precipitates formed at the time of casting or the time of forging form solid solutions whereby the ductility and toughness are improved.

(16) The low thermal expansion alloy having the chemical composition of the present invention has a low thermal expansion coefficient with a mean thermal expansion coefficient at 0 to 30° C. of 0.5×10.sup.−6/° C. or less and is free of martensite transformation at −120° C., that is, has a martensite transformation temperature of −120° C. or less. According to the present invention, furthermore, it is also possible to obtain a low thermal expansion alloy with a mean thermal expansion coefficient at 0 to 30° C. of 0.1×10.sup.−6/° C. or less.

(17) After the solid solution treatment, if necessary, it is also possible to perform stress-relieving annealing holding the steel at 300 to 350° C. for 1 to 5 hr, then air cooling or other known heat treatment.

EXAMPLES

(18) A high frequency melting furnace was used to produce Y-blocks and ingots adjusted to have the chemical compositions shown in Table 1. After that, the Y-blocks were subjected to diffusion treatment and solid solution treatment to obtain castings and the ingots were subjected to diffusion treatment, hot forging, and solid solution treatment to obtain forgings. Test pieces for confirming martensite transformed structures and test pieces for measuring the thermal expansion coefficient were taken.

(19) The martensite transformed structures were confirmed by using liquid nitrogen to hold a test piece in −100° C. and −120° C. atmospheres for 15 minutes, then using an optical microscope to examine for any martensite transformed structures. The results are shown in Table 1.

(20) The low thermal expansion alloy of the present invention was low in thermal expansion coefficient and further was free from martensite transformed structures even at −120° C.

(21) As opposed to this, in the comparative examples, martensite transformed structures are formed at −100° C. or the thermal expansion coefficient becomes higher. The targeted characteristic was not able to be obtained in at least one of the same.

(22) TABLE-US-00001 TABLE 1 Formation of martensite Thermal Diffusion transformed expansion treatment structures coefficient Alloy Chemical constituents (%) Temp. Time −100° −120° .sup.α0 to 30° C. no. Class C Si Mn Ni Co Al Mg Ca Ce La (° C.) (Hr) C. C. (ppm/° C.) 1 Forging — — — 33.55 3.27 — — — — — 1250 50 No No −0.32 Inv. ex. 1 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No −0.26 Inv. ex. 2 Forging — — — 33.74 1.69 — — — — — 1100 10 No No 0.22 Inv. ex. 2 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.31 Inv. ex. 3 Forging — — — 34.25 1.75 — — — — — — — No No 0.28 Inv. ex. 3 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.36 Inv. ex. 4 Forging — — — 33.01 4.88 — — — — — 1150 25 No No 0.19 Inv. ex. 4 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.27 Inv. ex. 5 Forging — — — 33.48 4.79 — — — — — 1200 15 No No 0.35 Inv. ex. 5 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.44 Inv. ex. 6 Forging 0.015 0.15 0.27 33.82 1.79 0.13 0.056 0.009 0.017 0.008 1200 25 No No 0.34 Inv. ex. 6 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.39 Inv. ex. 7 Forging 0.003 0.09 0.08 33.70 3.05 0.05 0.024 0.007 0.022 0.012 — — No No −0.05 Inv. ex. 7 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.04 Inv. ex. 8 Forging 0.007 0.08 0.08 33.31 3.00 0.09 0.032 0.010 0.025 0.014 1250 50 No No −0.24 Inv. ex. 8 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No −0.18 Inv. ex. 9 Forging 0.012 0.16 0.31 33.75 3.52 0.10 0.048 0.012 0.021 0.012 — — No No 0.22 Inv. ex. 9 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.31 Inv. ex. 10 Forging 0.003 0.09 0.15 33.33 3.93 0.11 0.041 0.008 0.019 0.008 1150 50 No No −0.04 Inv. ex. 10 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.03 Inv. ex.

(23) TABLE-US-00002 TABLE 2 (Continuation of Table 1) Occurrence of martensite thermal Diffusion transformed expansion treatment microstructure coefficient Alloy Chemical constituents (%) Temp. Time −100° −120° .sup.α0 to 30° C. no. Class C Si Mn Ni Co Al Mg Ca Ce La (° C.) (Hr) C. C. (ppm/° C.) 11 Forging 0.025 0.24 0.25 33.15 4.88 0.08 0.066 0.007 0.026 0.014 1100 50 No No 0.37 Inv. ex. 11 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.44 Inv. ex. 12 Forging 0.011 0.22 0.21 33.42 4.72 0.16 0.073 0.011 0.019 0.010 1300 10 No No 0.12 Inv. ex. 12 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.15 Inv. ex. 13 Forging — — — 32.66 5.11 — — — — — 1200 10 Yes — 0.35 Comp. ex. 13 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ Yes — 0.41 Comp. ex. 14 Forging — — — 33.77 5.24 — — — — — — — No No 0.75 Comp. ex. 14 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.81 Comp. ex. 15 Forging — — — 33.50 1.13 — — — — — — — Yes — 0.25 Comp. ex. 15 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ Yes — 0.30 Comp. ex. 16 Forging — — — 34.55 1.39 — — — — — 1150 50 No No 0.55 Comp. ex. 16 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.59 Comp. ex. 17 Forging 0.003 0.35 0.27 33.68 4.51 0.07 0.067 0.013 0.029 0.016 1200 25 No No 0.66 Comp. ex. 17 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.75 Comp. ex. 18 Forging 0.052 0.25 0.11 33.18 5.21 0.17 0.042 0.008 0.045 0.022 — — No No 0.62 Comp. ex. 18 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ No No 0.71 Comp. ex. 19 Forging 0.007 0.08 0.18 32.81 2.91 0.12 0.039 0.009 0.033 0.012 1250 50 Yes — −0.11 Comp. ex. 19 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ Yes — −0.02 Comp. ex. 20 Forging 0.004 0.17 0.61 33.31 1.43 0.23 0.027 0.054 0.028 0.011 1150 50 Yes — 0.17 Comp. ex. 20 Casting ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ ″ Yes — 0.26 Comp. ex.