JPH0137465B2 - - Google Patents
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- Publication number
- JPH0137465B2 JPH0137465B2 JP16803281A JP16803281A JPH0137465B2 JP H0137465 B2 JPH0137465 B2 JP H0137465B2 JP 16803281 A JP16803281 A JP 16803281A JP 16803281 A JP16803281 A JP 16803281A JP H0137465 B2 JPH0137465 B2 JP H0137465B2
- Authority
- JP
- Japan
- Prior art keywords
- amount
- alloy
- melting
- manganese
- titanium group
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
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- 239000011572 manganese Substances 0.000 claims description 45
- 229910045601 alloy Inorganic materials 0.000 claims description 34
- 239000000956 alloy Substances 0.000 claims description 34
- 230000008018 melting Effects 0.000 claims description 26
- 238000002844 melting Methods 0.000 claims description 26
- 239000010936 titanium Substances 0.000 claims description 20
- 239000000203 mixture Substances 0.000 claims description 17
- 229910000914 Mn alloy Inorganic materials 0.000 claims description 11
- 229910010389 TiMn Inorganic materials 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical group [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 238000013329 compounding Methods 0.000 claims description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims 3
- 239000001257 hydrogen Substances 0.000 description 10
- 229910052739 hydrogen Inorganic materials 0.000 description 10
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 9
- 238000001704 evaporation Methods 0.000 description 9
- 230000008020 evaporation Effects 0.000 description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 8
- 239000011232 storage material Substances 0.000 description 7
- 229910052786 argon Inorganic materials 0.000 description 4
- 238000000034 method Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005338 heat storage Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- YZCKVEUIGOORGS-OUBTZVSYSA-N Deuterium Chemical compound [2H] YZCKVEUIGOORGS-OUBTZVSYSA-N 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- -1 TiMn 1.5 Chemical compound 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 239000011575 calcium Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 229910052805 deuterium Inorganic materials 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 150000004678 hydrides Chemical class 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Description
本発明は、チタン族元素（Ti、Zr、Hf）とマ
ンガンとの２元系合金、例えばTiMn1.5、
ZrMn2、あるいはTi族元素とMnとを主成分とす
るTi族−Mn多元系合金の工業的製造法に関し、
詳しくは、加えたエネルギー量と理論上のMn量
に対応した一定割合のMnを、あらかじめ追加し
て配合し、しかる後アーク炉または高周波炉で溶
解することによつて、均質で、所望の理論組成を
有した良好な合金を容易に、経済的に得る方法を
提供するものである。
最近、水素貯蔵用材料、蓄熱材料、水素精製媒
体、重水素分離用媒体などの水素との反応を利用
した用途にTi族−Mn系合金の需要が高まつてい
る。しかし、Mnは本来その融点（1224±２℃）
付近で約1torr、1500℃で約25torr、1800℃で約
200torrの高い蒸気圧を有すると同時に、酸素や
窒素との親和力が強いため、Mnの蒸発による組
成ずれや不純物形成による偏析を起こす。特に、
Mn以上に反応性に富み、活性なTi族元素との合
金は、Mnをベースとする合金の溶解の中でも、
極めて難しいとされていた。
現在、炉内雰囲気や、その圧力、溶湯と接する
耐火物の改良などで、Mn基合金の製造法は幾分
向上しているものの、なお解決し得ない多くの問
題点を残している。
従来、これらの諸問題のうち、特に重要なMn
の組成ずれを解決するため、あらかじめ、Mnの
蒸発を考慮して、Mnを若干多めに配合する場合
もあつた。しかし、この追加量は、長年の熟練者
の経験に頼らざるを得ず、そのため、所望合金の
組成や、溶解温度、溶解時間、溶解量などによつ
て、出来上り合金の品質や組成が大きく変化し、
再現性のある高品質の合金を安定に供給すること
ができなかつた。
そこで、本発明者らはこの問題を解決するため
に、単位重量を溶解するために加えるべき電気的
エネルギー量と、合金組成式から得られる溶解合
金中の理論上のMn量とに着目して、種々検討し
た結果、良質で、所望の組成の合金を再現性よく
得るための指針となる関係式を得ることができ、
この式によつて高品質で、所望の理論組成の合金
を工業的規模で経済的に得られることを見出し
た。すなわち、本発明はカルシウム系組成物や、
ジルコニア、窒化ケイ素などの特殊るつぼを使用
した高周波溶解や、プラズマアークやアルゴンア
ーク溶解などのアークを熱源としたアーク溶解に
おいて、所望の化学式から理論的に得られるMn
量に加えて、以下の式から得られるMn量を追加
配合し、溶解する方法である。
追加Mn量＝Ｍ×Ｅ×ａ
ここで、Ｍは配合組成式から得られる理論上の
Mn量、Ｅは合金１Kgを溶解するために、加える
エネルギー量（単位：KW・ｈ／Kg）、ａは（1.1
〜34）×10-4（Kg／KW・ｈ）
本発明者らは、先にアークを熱源としたアーク
溶解炉を用いた高品質Ti族−Mn系合金の製造方
法を提案した。これは、溶解時に最適な印加エネ
ルギー量（上記Ｅの値）を限定したものであつた
が、本発明はこれを更に発展させたものである。
すなわち、極めて活性なMnとTiを主成分とす
るTi族−Mn系合金の超高温での溶解で最も問題
となるのはMnの蒸発である。一般に、Mnの蒸
発量を左右する因子としては、炉内雰囲気圧
力、熱エネルギー発生のための電力量（KW）、
溶解時間（hour）、溶解合金量（Kg）などで
ある。脱ガスを目的とする場合には、減圧が望ま
しいが、Mnの蒸発を少なくするには、加圧状態
が好ましい。このことを鑑み、一般には炉内圧は
30torr〜1.5気圧程度がよい。この程度に炉内雰
囲気圧力を設定すれば、上記因子による影響は
それ程多くはない。従つてMnの蒸発量の多少は
上記、、に依るところが大きく、これらの
影響力はKW・ｈ／Kgの値、すなわち、単位合金
溶解量当りに加えた電気的エネルギーの総量（前
記Ｅ値）の大小によつて評価され得る。換言すれ
ば、熱エネルギー発生のための電力（KW）が大
きい程、また溶解時間（ｈ）が長い程、そして溶
解合金量（Kg）が少ない程、単位重量当りに受け
る全エネルギー量が大きくなり、Mnの蒸発量は
大きい。
そこで、本発明者らは上記Ｅの値を種々変化さ
せながら、Mn蒸発量を検討した結果、合金組成
中の理論Mn量、および上記Ｅ値にほぼ比例し
て、溶解中のMnが蒸発することがわかつた。ま
たこの時の比例係数ａは、
ａ＝（1.1〜34）×10-4（Kg／KW・ｈ）
の範囲にあり、特に、TiMn1.5合金を溶解する場
合には、ａ＝（3.8〜20）×10-4（Kg／KW・ｈ）が
最も優れていた。このことは、あらかじめ、原材
料の仕込み時にＭ×Ｅ×ａ分だけ、余計に追加し
て配合しておけば、溶解後に所望の理論組成の合
金を得ることができることを示している。
なお、ここでは追加Mn量に対する蒸発分を考
慮していない。これを考慮すれば、全追加Mn量
は（Ｍ＋計算した追加量）×Ｅ×ａとなる。しか
し、追加量が、通常、組成式から得られる理論
Mn量の数％以内であるから、この量は無視して
もよい。
以下に本発明の実施例を示す。
実施例 １
アルゴンアーク溶解炉によつて、TiMn1.5合金
を、炉内アルゴン雰囲気圧45torrで溶解した。溶
解原料は、Ti、Mnともに99％以上の純金属を用
い、溶解後は、水冷銅るつぼ中でそのまま凝固し
た。第１表に４種類の単位重量当りの電気エネル
ギー量に関して、Mnを追加しなかつた時の溶解
後のMnの歩留り（％）、および４種類のａ値に
従つて、Mnを追加した場合の溶解後のMn量を、
理論式から得られる合金中のMn量に対する割合
（％）として示す。
The present invention provides a binary alloy of titanium group elements (Ti, Zr, Hf) and manganese, such as TiMn 1.5 ,
Regarding the industrial manufacturing method of ZrMn 2 or Ti group-Mn multi-component alloy whose main components are Ti group elements and Mn,
Specifically, by adding a certain proportion of Mn corresponding to the amount of energy applied and the theoretical amount of Mn, and then melting it in an arc furnace or high-frequency furnace, a homogeneous and desired theoretical amount can be obtained. The present invention provides a method for easily and economically obtaining an alloy having a good composition. Recently, demand for Ti group-Mn alloys has been increasing for applications that utilize reactions with hydrogen, such as hydrogen storage materials, heat storage materials, hydrogen purification media, and deuterium separation media. However, Mn originally has its melting point (1224±2℃)
Approximately 1 torr at nearby temperatures, approximately 25 torr at 1500℃, approximately 25torr at 1800℃
It has a high vapor pressure of 200 torr and at the same time has a strong affinity with oxygen and nitrogen, which causes composition shifts due to evaporation of Mn and segregation due to the formation of impurities. especially,
Alloys with Ti group elements, which are more reactive and active than Mn, are the most active in the melting of Mn-based alloys.
It was considered extremely difficult. Currently, the manufacturing method for Mn-based alloys has improved somewhat by improving the furnace atmosphere, its pressure, and the refractories that come into contact with the molten metal, but many problems still remain that cannot be resolved. Conventionally, among these problems, Mn
In order to resolve the compositional deviation, there were cases in which a slightly larger amount of Mn was added in advance, taking Mn evaporation into consideration. However, this additional amount must be determined by the experience of a skilled worker over many years, and as a result, the quality and composition of the finished alloy can vary greatly depending on the desired alloy composition, melting temperature, melting time, melting amount, etc. death,
It has not been possible to stably supply reproducible, high-quality alloys. Therefore, in order to solve this problem, the present inventors focused on the amount of electrical energy that should be applied to melt a unit weight and the theoretical amount of Mn in the melted alloy obtained from the alloy composition formula. As a result of various studies, we were able to obtain a relational expression that serves as a guideline for obtaining a high-quality alloy with a desired composition with good reproducibility.
It has been found that by using this formula, an alloy of high quality and a desired theoretical composition can be obtained economically on an industrial scale. That is, the present invention provides calcium-based compositions,
Mn can be theoretically obtained from a desired chemical formula in high-frequency melting using special crucibles such as zirconia or silicon nitride, or in arc melting using an arc as a heat source such as plasma arc or argon arc melting.
In this method, the amount of Mn obtained from the following formula is added and dissolved. Additional Mn amount = M x E x a Here, M is the theoretical value obtained from the compounding composition formula.
The amount of Mn, E is the amount of energy added to melt 1 kg of alloy (unit: KW・h/Kg), a is (1.1
〜34)×10 −4 (Kg/KW·h) The present inventors previously proposed a method for manufacturing a high-quality Ti group-Mn alloy using an arc melting furnace using an arc as a heat source. This limited the optimum amount of energy to be applied during melting (the above value of E), but the present invention further develops this. In other words, the most problematic problem in melting Ti group-Mn alloys containing extremely active Mn and Ti as main components at ultrahigh temperatures is the evaporation of Mn. In general, the factors that affect the amount of Mn evaporation are the atmospheric pressure in the furnace, the amount of electricity (KW) for generating thermal energy,
These include melting time (hour) and amount of melted alloy (Kg). For the purpose of degassing, reduced pressure is desirable, but for reducing evaporation of Mn, pressurized state is preferred. Considering this, generally the furnace pressure is
Approximately 30 torr to 1.5 atm is good. If the atmospheric pressure in the furnace is set to this level, the influence of the above factors will not be so great. Therefore, the amount of evaporation of Mn largely depends on the above, and these influences are the value of KW・h/Kg, that is, the total amount of electrical energy added per unit amount of melted alloy (the above E value) can be evaluated based on the size of In other words, the greater the electric power (KW) for generating thermal energy, the longer the melting time (h), and the lower the amount of melted alloy (Kg), the greater the total amount of energy received per unit weight. , the amount of evaporation of Mn is large. Therefore, the present inventors investigated the amount of Mn evaporation while varying the value of E, and found that Mn in the melt evaporates approximately in proportion to the theoretical amount of Mn in the alloy composition and the E value above. I found out. In addition, the proportionality coefficient a at this time is in the range of a=(1.1~34)×10 -4 (Kg/KW・h), and especially when melting TiMn 1.5 alloy, a=(3.8~20 )×10 -4 (Kg/KW・h) was the best. This shows that if an extra amount of M×E×a is added and blended in advance at the time of preparing the raw materials, it is possible to obtain an alloy with a desired theoretical composition after melting. Note that here, the evaporation amount with respect to the amount of additional Mn is not considered. Taking this into consideration, the total amount of additional Mn is (M+calculated additional amount)×E×a. However, the additional amount is usually derived from the theoretical formula.
Since it is within several percent of the Mn amount, this amount can be ignored. Examples of the present invention are shown below. Example 1 A TiMn 1.5 alloy was melted in an argon arc melting furnace at an argon atmosphere pressure of 45 torr. The melted raw materials used were pure metals with Ti and Mn both containing 99% or more, and after melting, they were solidified in a water-cooled copper crucible. Table 1 shows the yield (%) of Mn after melting when no Mn is added, and the yield (%) when Mn is added, according to the four types of a values, regarding the amount of electrical energy per unit weight for four types. The amount of Mn after dissolution is
It is expressed as a ratio (%) to the amount of Mn in the alloy obtained from the theoretical formula.
【表】
第１表に示したように、本発明によれば、溶解
後に得られた合金中のMn量は、理論値に対して
その差±0.6％以内に入つており、ほぼ所望の組
成の合金を得ることができた。
実施例 ２
プラズマアーク溶解炉を用いて、直径10cm、高
さ10cmのTi0.5Zr0.5Mn1.9合金を溶解した。雰囲気
ガスはアルゴンで、炉内圧力は約１気圧とした。
実施例１と同様の形式で、その結果を第２表に示
す。[Table] As shown in Table 1, according to the present invention, the amount of Mn in the alloy obtained after melting is within ±0.6% of the theoretical value, and almost has the desired composition. We were able to obtain an alloy of Example 2 A Ti 0.5 Zr 0.5 Mn 1.9 alloy with a diameter of 10 cm and a height of 10 cm was melted using a plasma arc melting furnace. The atmospheric gas was argon, and the pressure inside the furnace was approximately 1 atm.
The results are shown in Table 2 in the same format as Example 1.
【表】
第２表のように、プラズマアーク溶解によつて
も、溶解後に得られた合金中のMn量は、理論値
に対してその差±0.5％以内に入つており、ほぼ
所望の組成式のTi0.5Zr0.5Mn1.9合金を得ることが
できた。
実施例 ３
ZrO2のるつぼを用いて、高周波溶解によつて、
TiMn1.5合金を製造した。炉内雰囲気ガスはアル
ゴンで、その圧力は55torrであり、出来上り合金
塊の重量は約50Kgであつた。本発明の効果を用途
面から評価するため、この実施例によつて得られ
た合金を水素化し、水素貯蔵用材料としての特性
を測定した。その結果の一例を図面に示す。
図は横軸にａ値を、縦軸に水素貯蔵材の特性と
して最も重要な大気圧下へ室温（約20℃）で放出
した水素量（ml／ｇ）を示したものである。図に
見られるように、係数ａ＝（1.1〜34）×10-4（Kg／
KW・ｈ）の範囲では、放出水素量が、150ml／
ｇ以上を有し、TiMn1.5が水素貯蔵材として優れ
ていることがわかる。また、特にａ＝（3.8〜20）
×10-4（Kg／KW・ｈ）の範囲では180ml／ｇ以上
を示し、特に優れた合金を得ることができた。
以上の実施例に見られるように、本発明はTi
族元素と、Mnを主成分とするTi族−Mn系合金
の提供するものである。通常の金属間化合物と異
なる非化学量論組成であるTi族−マンガン系合
金の性能を安定して製造するためにMnの組成を
式Ｍ・Ｅ・αでコントロールすることにより、
Mnの組成ずれが±0.6％以内である高品質な合金
塊を、容易に、経済的に得ることができる。この
ように、本発明により、水素貯蔵材や蓄熱材とし
て好適な、高品質のTi族−Mn系合金を比較的安
価に、しかも安定して製造することができる。[Table] As shown in Table 2, even with plasma arc melting, the amount of Mn in the alloy obtained after melting is within ±0.5% of the theoretical value, and almost has the desired composition. A Ti 0.5 Zr 0.5 Mn 1.9 alloy of formula could be obtained. Example 3 Using a ZrO 2 crucible, by high frequency melting,
A TiMn 1.5 alloy was produced. The atmospheric gas in the furnace was argon, its pressure was 55 torr, and the weight of the finished alloy ingot was about 50 kg. In order to evaluate the effects of the present invention from a usage perspective, the alloy obtained in this example was hydrogenated and its properties as a hydrogen storage material were measured. An example of the results is shown in the drawing. In the figure, the horizontal axis shows the a value, and the vertical axis shows the amount of hydrogen (ml/g) released into atmospheric pressure at room temperature (approximately 20°C), which is the most important characteristic of hydrogen storage materials. As seen in the figure, coefficient a=(1.1~34)× 10-4 (Kg/
KW・h), the released hydrogen amount is 150ml/
It can be seen that TiMn 1.5 is excellent as a hydrogen storage material. Also, especially a = (3.8 ~ 20)
In the range of ×10 -4 (Kg/KW·h), it showed 180 ml/g or more, and a particularly excellent alloy could be obtained. As seen in the above examples, the present invention
The present invention provides a Ti group-Mn alloy containing a Ti group element and Mn as main components. In order to stably produce the performance of Ti group-manganese alloy, which has a non-stoichiometric composition different from that of ordinary intermetallic compounds, by controlling the Mn composition using the formula M・E・α,
A high-quality alloy ingot with a Mn composition deviation within ±0.6% can be obtained easily and economically. As described above, according to the present invention, a high quality Ti group-Mn alloy suitable as a hydrogen storage material or a heat storage material can be produced stably at a relatively low cost.
図面は本発明の実施例として、TiMn1.5合金に
ついて適用した場合のTiMn1.5水素化物の水素貯
蔵特性を、比例係数ａに対して示した図である。
The drawing is a diagram showing the hydrogen storage characteristics of a TiMn 1.5 hydride when applied to a TiMn 1.5 alloy as an example of the present invention, with respect to the proportionality coefficient a.
Claims (1)
族−マンガン系合金を、高周波あるいはアークを
熱源とする溶解炉を用いて製造する際、式Ｍ・
Ｅ・ａ（ただし、Ｍは配合組成式から得られる合
金中の理論上のマンガン量、Ｅは溶解熱を発生さ
せるために印加するべき合金単位重量当りのエネ
ルギー量（KW・ｈ／Kg）、ａは（1.1〜34）×10-4
（Kg／KW・ｈ）である。）で表される量だけあら
かじめマンガンの仕込み量を追加して配合し、溶
解することを特徴とするチタン族−マンガン系合
金の製造法。 ２ チタン族−マンガン系合金がTiMn1.5である
特許請求の範囲第１項記載のチタン族−マンガン
系合金の製造法。 ３ ａ＝（3.8〜20）×10-4（Kg／KW・ｈ）である
特許請求の範囲第２項記載のチタン族−マンガン
系合金の製造法。[Claims] 1. When manufacturing a titanium group-manganese alloy whose main components are titanium group and manganese using a melting furnace using a high frequency or an arc as a heat source, the formula M.
E・a (where M is the theoretical amount of manganese in the alloy obtained from the compounding composition formula, E is the amount of energy per unit weight of the alloy that should be applied to generate heat of melting (KW・h/Kg), a is (1.1~34)×10 -4
(Kg/KW・h). ) A method for producing a titanium group-manganese alloy, which is characterized in that an amount of manganese is added and mixed in advance in an amount expressed by the formula, and then melted. 2. The method for producing a titanium group-manganese alloy according to claim 1, wherein the titanium group-manganese alloy is TiMn 1.5 . 3. The method for producing a titanium group-manganese alloy according to claim 2, wherein a=(3.8-20)×10 −4 (Kg/KW·h).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56168032A JPS5871345A (en) | 1981-10-21 | 1981-10-21 | Manufacture of titanium group metal-manganese alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56168032A JPS5871345A (en) | 1981-10-21 | 1981-10-21 | Manufacture of titanium group metal-manganese alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5871345A JPS5871345A (en) | 1983-04-28 |
| JPH0137465B2 true JPH0137465B2 (en) | 1989-08-07 |
Family
ID=15860549
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP56168032A Granted JPS5871345A (en) | 1981-10-21 | 1981-10-21 | Manufacture of titanium group metal-manganese alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5871345A (en) |
-
1981
- 1981-10-21 JP JP56168032A patent/JPS5871345A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5871345A (en) | 1983-04-28 |
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